Hot fill process with closures made from bimodal polyethylene compositions

ABSTRACT

Bimodal polyethylene compositions for use in hot-fill closures and processes.

The present disclosure relates to a hot filling process which employs closures made from bimodal polyethylene compositions.

Hot filling techniques are commonly used in the bottling of beverages such as, for example, drinks, fruit juices, milk, tea, sports drinks and flavored water. Typically, the material employed to package these materials in a hot fill application is polyethylene terephthalate (PET). PET bottles are light weight and tough.

A typical hot fill process involves the following steps. A hot liquid beverage is added to a plastic bottle while at an elevated temperature, typically from about 70 to about 93° C. under a positive pressure and over a 15 to 30 second time interval. The bottle or container is then immediately sealed with a plastic closure and tilted on its side or inverted. Contact of the hot liquid with the closure sterilizes the closure. Inversion may last for example, about 15 seconds, or a time sufficient for sterilization of the closure interior. Following sterilization of the closure interior, the bottle may cooled to for example about 40° C.

In order to be properly applicable to a hot filling process the closure should be made of a material that imparts heat resistance (e.g., resistance to deformation during hot/cold cycles occurring in a hot filling process), good sealing properties to prevent leaking, and resistance to the development of cracks.

As discussed in a recent ANTEC® publication, “Deformation Measurement, Modeling and Morphology Study for HDPE Caps and Closures”, by XiaoChuan (Alan) Wang, Mar. 23-25, 2015, Orlando, Fla., USA, it is difficult to directly study the deformation properties of plastic closures due to their complex geometries and relatively small dimensions. Standard tests for creep properties (e.g., tensile creep, flexural creep, and compressive creep) such as those described in ASTM D-2990 employ standard compression molded specimens or plaques, not caps or closures per se. Further, the final polymer morphology, as it exists in a molded closure formed from injection molding or continuous compression molding techniques, may not be represented when using standardized testing which employ standardized plaques. As such, a method which informs about the deformation properties of a finished closure was developed. The method employed a model to evaluate the deformation of an “as is closure” at different instantaneous stresses, times and temperatures. To properly model the closure deformation, any tamper-evident ring attached to the closure was removed.

We have now found that application of the methodology and model to closures comprising high density polyethylene compositions allows one to select for polymer compositions which are particularly suitable for application in hot fill closures and processes.

The present disclosure shows that certain bimodal polyethylene compositions are suitable for making closures used in hot fill processes.

The preset disclosure also contemplates the use of bimodal polyethylene compositions for use in aseptic fill processes.

A recently developed model and a series of tests are used to demonstrate those closure characteristics which are suitable for hot fill, or aseptic fill applications. Provided is a process to fill a container, the process comprising: adding a hot liquid to the container through a container opening, sealing the container opening with a closure comprising a bimodal polyethylene composition, and bringing the hot liquid into contact with an interior surface of the closure; wherein the bimodal polyethylene composition comprises:

(1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and

(2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0; a density of at least 0.949 g/cm³, a melt index I₂, of from 0.2 to 3.0 g/10 min; an M_(z) of less than 500,000; a stress exponent of less than 1.53, and an ESCR Condition B (10% IGEPAL) of at least 20 hrs.

Provided is a use of a closure in a hot fill process, wherein the closure comprises a bimodal polyethylene composition comprising:

(1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and

(2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0; a density of at least 0.949 g/cm³, a melt index I₂, of from 0.2 to 3.0 g/10 min; an M_(z) of less than 500,000; a stress exponent of less than 1.53, and an ESCR Condition B (10% IGEPAL) of at least 20 hrs.

Provided is a process to fill a container, the process comprising: adding a hot liquid to the container through a container opening; sealing the container opening with a closure comprising a bimodal polyethylene composition having a density of from 0.949 g/cm³ to 0.960 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min; and bringing the hot liquid into contact with an interior surface of the closure; wherein the closure has a time exponent, m of 0.105 or less where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

Provided is a use for a closure in a hot fill process, wherein the closure comprises a bimodal polyethylene composition having a density of from 0.949 g/cm³ to 0.960 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min, wherein the closure has a time exponent, m of 0.105 or less, where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; 6 is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

Provided is a process to fill a container, the process comprising: adding a hot liquid to the container through a container opening; sealing the container opening with a closure comprising a bimodal polyethylene composition having a density of at least 0.949 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min; and bringing the hot liquid into contact with an interior surface of the closure; wherein the closure has a time exponent, m of 0.105 or less where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

Provided is a use for a closure in a hot fill process, wherein the closure comprises a bimodal polyethylene composition having a density of at least 0.949 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min, wherein the closure has a time exponent, m of 0.105 or less, where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1A shows a gel permeation chromatograph for the unimodal polyethylene composition used in Example 1.

FIG. 1B shows a gel permeation chromatograph for the bimodal polyethylene composition used in Example 2.

FIG. 2A shows a plan view of the probe used in the closure deformation testing. The view shows the bottom side of the probe which contacts the upper surface of the closure

FIG. 2B shows a partially transparent perspective view of the probe used in the closure deformation testing.

FIG. 3 shows a plan view (with screw locations indicated) of the closure holder used in deformation stress testing. The view shows the upper surface of the holder which receives the lower annular edge of the closure.

FIG. 4 shows actual and fitted compressive deformation data for the closures of Example 1 and Example 2.

DETAILED DESCRIPTION

Filling Process

The present disclosure is concerned with the use of closures in filling/sealing processes which have at least one step in which the closure interior (and optionally the container, bottle and the like) is (are) contacted with a liquid at elevated temperatures, or temperatures above ambient, or above room temperature or above about 20° C., or any temperature high enough to destroy microorganisms which may lead to illness when consumed (e.g., temperatures high enough to sterilize the closure and/or pasteurize the liquid). Processes which involve steps in which a closure is used to seal a container, bottle and the like containing a liquid at an elevated temperature include for example hot fill processes and in some cases aseptic fill processes. The disclosure is not limited to any particular end use or process so long as a closure is contacted with a liquid at elevated temperatures for the end use or during the process and is used to seal a container, bottle and the like.

In the present disclosure the terms “hot liquid” and “hot beverage” are used interchangeably, and connote that a liquid that has been heated to above ambient temperature or room temperature or above about 20° C., or any temperature high enough to destroy microorganisms which may lead to illness when consumed (e.g., temperatures high enough to pasteurize the liquid or beverage).

In embodiments of the disclosure, a hot liquid is a liquid that has been heated to from about 21° C. to about 150° C., and further including all numbers and narrower ranges within this range such as for example from about 70° C. to about 150° C., or from about 70° C. to about 145° C., or from about 80° C. to about 150° C., or from about 80° C. to about 145° C., or from about 21° C. to about 100° C., or from about 30° C. to about 100° C., or from about 30° C. to about 98° C., or from about 30° C. to about 95° C., or from about 30° C. to about 93° C., or from about 50° C. to about 100° C., or from about 50° C. to about 98° C., or from about 50° C. to about 95° C., or from about 50° C. to about 93° C., or from about 60° C. to about 100° C., or from about 60° C. to about 98° C., or from about 60° C. to about 95° C., or from about 60° C. to about 93° C., or from about 70° C. to about 100° C., or from about 70° C. to about 98° C., or from about 70° C. to about 95° C., or from about 70° C. to about 93° C.

The term “interior surface” as it is applied to a cap or closure is any part of the closure interior that may come into contact with a hot liquid during a filling process.

An embodiment of the disclosure is a process to fill a container, the process comprising: adding a hot liquid to the container through a container opening, sealing the container opening with a closure comprising a bimodal polyethylene composition, and bringing the hot liquid into contact with an interior surface of the closure.

Hot Fill Process

A hot fill process is often used in an automated container filling line. Use of the hot fill process is often the process of choice for juices, beverages and the like since it eliminates the need for the addition of chemicals and preservatives while maintaining the same shelf life and nutritional properties of the beverage. Consumers are often wary of the presence of preservatives and chemicals, and so hot filling processes provide a useful alternative.

The hot filling process can be used in combination with any suitable beverages, including vegetable and fruit juice, dairy products such as milk, flavored waters, sports drinks and the like.

A hot fill process comprises a series of steps. Ideally the steps are optimized to provide shorter container fill times while still providing acceptable beverage shelf life in the absence of added chemicals or preservatives. The steps are generally incorporated into a container or bottle fill line and generally comprise:

Step 1) A beverage is heated to the desired hot filling temperature. The temperatures employed are not specifically defined herein, but by way of non-limiting example only, can be from about 70° C. to about 95° C. Suitable temperatures include those which are known to kill microorganisms which may cause illness (e.g., temperatures at which the beverage or liquid is pasteurized). The beverage may be heated using any known device, such as but not limited to a heat exchanger, and may be heated in a continuous or batch manner. The beverage may be heated for any suitable time which is known to kill microorganisms which may be present in the liquid. By way of a non-limiting examples, the beverage may be heated by passage through a heat exchanger for at least 10, or at least 15, or at least 20 seconds.

Step 2) A container is filled with the hot beverage using a suitable filling apparatus, followed by the addition of a closure. By hot filling the container, the container interior is sterilized by the hot beverage. Although the closure should be added immediately once the container is hot filled, nitrogen may be introduced into the head space to displace unwanted oxygen prior to the addition of the closure. Optionally, and before the container is filled with the hot beverage, the temperature of the liquid may be reduced slightly. By way of providing a non-limiting example only, the temperature of the beverage may be reduced to from about 80° C. to about less than 90° C.

Step 3) The container is tilted or inverted, or the bottle/closure system moved somehow, so as to bring the hot beverage into contact with the interior surface of the closure. Bringing the hot beverage into contact with the closure interior sterilizes the container interior surfaces.

Step 4) The sealed beverage container and closure may be cooled using a suitable cooling station or apparatus, such as but limited to a shower station or a cooling bath. In embodiments of the disclosure, the container-closure-beverage system is cooled to ambient temperatures or below. In order to preserve the beverage freshness and/or taste, in some embodiments, it may be preferable to rapidly cool the container-closure-beverage system. When cooling the sealed container, a vacuum may be created inside the container, further minimizing bacterial growth. Step 4 may also be considered as optional.

Other container fill line process steps known in the art may be used in combination with the above hot fill process steps. For example, the above hot fill process steps may be followed by further cooling, drying and labeling steps.

Container (e.g. Bottle)

The material used for the container (e.g., bottle) is not specifically defined, but by way of providing a non-limiting example only, the material may be polyethylene terephthalate (PET). In another embodiment the container (e.g., bottle) may be made of glass.

Closure

A closure as described in the present disclosure is a closure suitable for use in a container sealing process comprising one more steps in which the closure comes into contact with a liquid at elevated temperatures, such as a hot fill processes, and in some cases aseptic fill processes.

The terms “cap” and “closure” are used interchangeably in the current disclosure, and both connote any suitably shaped molded article for enclosing, sealing, closing or covering etc., a suitably shaped opening, a suitably molded aperture, an open necked structure or the like used in combination with a container, a bottle, a jar, a pouch and the like.

In an embodiment of the disclosure, the polymer compositions described below are used in the formation of molded articles. For example, articles formed by continuous compression molding and injection molding are contemplated. Such articles include, for example, caps, screw caps, and closures for bottles.

Without wishing to be bound by theory, the instantaneous compressive deformation of an “as-is” closure is a function of both instantaneous force (e.g., stress) and time in a non-linear relationship at a given temperature and modeling is required to elucidate the underlying structure-property relationships. The instantaneous compressive deformation model employed in the current disclosure is a compressive strain model represented by the following equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm² and t is the loading time in seconds. A is the model coefficient; parameter n is termed the “deformation stress exponent” and m is termed the “time exponent”. Any software capable of performing non-linear regressions can be used to estimate the model parameters. Such a compressive deformation model was recently disclosed at an ANTEC™ meeting as “Deformation Measurement, Modeling and Morphology Study for HDPE Caps and Closures”, XiaoChuan (Alan) Wang, Mar. 23-25, 2015, Orlando, Fla., USA.

In an embodiment of the present disclosure, a closure has a time exponent, m of 0.105 or less where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

In further embodiments of the present disclosure, a closure has a time exponent, m of 0.105 or less, or ≤0.0955, or ≤0.0910, or ≤0.0875, or ≤0.0850, or ≤0.0825, or ≤0.0800, or ≤0.0790, where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

In an embodiment of the present disclosure, the closure comprises a bimodal polyethylene composition having a density of from 0.949 g/cm³ to 0.960 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min.

In an embodiment of the present disclosure, the closure comprises a bimodal polyethylene composition having a density of at least 0.949 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min.

In an embodiment of the disclosure, a bimodal polymer composition is used in the formation of any closure, of any suitable design and dimensions for use in any hot filling process for filling any suitable bottle, container or the like.

In an embodiment of the disclosure, the bimodal polyethylene compositions described below are used in the formation of a closure for bottles, containers, pouches and the like. For example, closures for bottles formed by continuous compression molding, or injection molding are contemplated. Such closures include, for example, hinged caps, hinged screw caps, hinged snap-top caps, and hinged closures for bottles, containers, pouches and the like.

In an embodiment of the disclosure, a closure (or cap) is a screw cap for a bottle, container, pouches and the like.

In an embodiment of the disclosure, a closure (or cap) is a snap closure for a bottle, container, pouches and the like.

In an embodiment of the disclosure, a closure (or cap) comprises a hinge made of the same material as the rest of the closure (or cap).

In an embodiment of the disclosure, a closure (or cap) is hinged closure.

In an embodiment of the disclosure, a closure (or cap) is a hinged closure for bottles, containers, pouches and the like.

In an embodiment of the disclosure, a closure (or cap) is a flip-top hinge closure, such as a flip-top hinge closure for use on a plastic ketchup bottle or similar containers containing foodstuffs.

When a closure is a hinged closure, it comprises a hinged component and generally consists of at least two bodies which are connected by a thinner section that acts as a hinge allowing the at least two bodies to bend from an initially molded position. The thinner section may be continuous or web-like, wide or narrow.

A useful closure (for bottles, containers and the like) is a hinged closure and may consist of two bodies joined to each other by at least one thinner bendable portion (e.g., the two bodies can be joined by a single bridging portion, or more than one bridging portion, or by a webbed portion, etc.). A first body may contain a dispensing hole and which may snap onto or screw onto a container to cover a container opening (e.g., a bottle opening) while a second body may serve as a snap on lid which may mate with the first body.

The caps and closures, of which hinged caps and closures and screw caps are a subset, can be made according to any known method, including for example injection molding and compression molding techniques that are well known to persons skilled in the art. Hence, in an embodiment of the disclosure a closure (or cap) comprising the polyethylene composition (defined below) is prepared with a process comprising at least one compression molding step and/or at least one injection molding step.

In one embodiment, the closures (including single piece or multi-piece variants and hinged variants) are well suited for sealing bottles, containers and the like, for examples bottles that may contain drinkable water, and other foodstuffs, including but not limited to liquids that are under an appropriate pressure (i.e., carbonated beverages or appropriately pressurized drinkable liquids).

The closures and caps may also be used for sealing bottles containing drinkable water or non-carbonated beverages (e.g., juice). Other applications, include caps and closures for bottles, containers and pouches containing foodstuffs, such as for example ketchup bottles and the like.

The closures and caps may be one-piece closures or two piece closures comprising a closure and a liner.

The closures and caps may also be of multilayer design, wherein the closure of cap comprises at least two layers at least one of which is made of the bimodal polyethylene compositions described herein.

In an embodiment of the disclosure the closure is made by continuous compression molding.

In an embodiment of the disclosure the closure is made by injection molding.

Bimodal Polyethylene Compositions

In the present disclosure, the bimodal polyethylene compositions suitable for use in closures for filling processes such as a hot fill process (or any other filling process which comprises at least one step carried out at elevated temperature, such as is the case in some aseptic fill processes) may be chosen based on their tendency to give closures having a combination of good resistance to cracking, sealability and good compressive deformation properties. Direct methods which measure the properties of the closure itself may provide a more accurate representation of the real word performance of a given polyethylene composition for various end use applications.

The term “unimodal” is herein defined to mean there will be only one significant peak or maximum evident in a GPC-curve. A unimodal profile includes a broad unimodal profile. Alternatively, the term “unimodal” connotes the presence of a single maxima in a molecular weight distribution curve generated according to the method of ASTM D6474-99. In contrast, by the term “bimodal” it is meant that there will be a secondary peak or shoulder evident in a GPC-curve which represents a higher or lower molecular weight component (i.e. the molecular weight distribution, can be said to have two maxima in a molecular weight distribution curve). Alternatively, the term “bimodal” connotes the presence of two maxima in a molecular weight distribution curve generated according to the method of ASTM D6474-99. The term “multi-modal” denotes the presence of two or more maxima in a molecular weight distribution curve generated according to the method of ASTM D6474-99.

In an embodiment of the present disclosure, the bimodal polyethylene compositions are composed of at least two ethylene copolymer components: a first ethylene copolymer and a second ethylene copolymer.

Examples of bimodal polyethylene compositions which are useful in the present disclosure are disclosed in for example U.S. Pat. No. 8,962,755, and U.S. Patent Application Publication No. 2015-0353715 A1 and U.S. application Ser. No. 14/829,998, which are incorporated herein by reference in their entirety.

By the term “ethylene copolymer” it is meant that the copolymer comprises both polymerized ethylene and at least one polymerized alpha-olefin comonomer, with polymerized ethylene being the majority species.

The terms “homogeneous” or “homogeneously branched polymer” as used herein define homogeneously branched polyethylene which has a relatively narrow composition distribution, as indicated by a relatively high composition distribution breadth index (CDBI₅₀). That is, the comonomer is randomly distributed within a given polymer chain and a substantial portion of the polymer chains have same ethylene/comonomer ratio.

It is well known that metallocene catalysts and other so called “single site catalysts” incorporate comonomer more evenly than traditional Ziegler-Natta catalysts when used for catalytic ethylene copolymerization with alpha olefins. This fact is often demonstrated by measuring the composition distribution breadth index (CDBI₅₀) for corresponding ethylene copolymers. The composition distribution of a polymer can be characterized by the short chain distribution index (SCDI) or composition distribution breadth index (CDBI₅₀). The definition of composition distribution breadth index (CDBI₅₀) can be found in PCT publication WO 93/03093 and U.S. Pat. No. 5,206,075. The CDBI₅₀ is conveniently determined using techniques which isolate polymer fractions based on their solubility (and hence their comonomer content). For example, temperature rising elution fractionation (TREF) as described by Wild et al. J. Poly. Sci., Poly. Phys. Ed. Vol. 20, p 441, 1982 or in U.S. Pat. No. 4,798,081 can be employed. From the weight fraction versus composition distribution curve, the CDBI₅₀ is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 50% of the median comonomer content on each side of the median. Generally, Ziegler-Natta catalysts produce ethylene copolymers with a CDBI₅₀ of less than about 50 weight %, or less than about 55 weight %, consistent with a heterogeneously branched copolymer. In contrast, metallocenes and other single site catalysts will most often produce ethylene copolymers having a CDBI₅₀ of greater than about 55 weight %, or greater than about 60 weight %, consistent with a homogeneously branched copolymer. Alternatively, the CDBI₂₅, which is sometimes used in the art, is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 25% of the median comonomer content on each side of the median.

The First Ethylene Copolymer

In an embodiment of the disclosure, the first ethylene copolymer of the bimodal polyethylene composition has a density of from about 0.920 g/cm³ to about 0.955 g/cm³; a melt index, I₂, of less than about 0.4 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 3.0 and a weight average molecular weight, M_(w), that is greater than the M_(w) of the second ethylene copolymer. In an embodiment of the disclosure, the weight average molecular weight, M_(w), of the first ethylene copolymer is at least 110,000.

In an embodiment of the disclosure, the first ethylene copolymer of the bimodal polyethylene composition has a density of from about 0.920 g/cm³ to about 0.955 g/cm³; a melt index, I₂, of less than about 0.4 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 2.7 and a weight average molecular weight, M_(w), that is greater than the M_(w) of the second ethylene copolymer.

In an embodiment of the disclosure, the first ethylene copolymer is a homogeneously branched copolymer.

In an embodiment of the disclosure, the first ethylene copolymer is made with a single site catalyst, such as for example a phosphinimine catalyst.

In an embodiment of the disclosure, the comonomer (i.e. alpha-olefin) content in the first ethylene copolymer can be from about 0.05 to about 3.0 mol %. The comonomer content of the first ethylene polymer is determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In embodiments of the disclosure, the comonomer in the first ethylene copolymer is one or more olefin such as but not limited to 1-butene, 1-hexene, 1-octene and the like.

In an embodiment of the disclosure, the first ethylene copolymer is a copolymer of ethylene and 1-octene.

In an embodiment of the disclosure, the short chain branching in the first ethylene copolymer can be from about 0.25 to about 15 short chain branches per thousand carbon atoms (SCB1/1000 Cs). In further embodiments of the disclosure, the short chain branching in the first ethylene copolymer can be from 0.5 to 15, or from 0.5 to 12, or from 0.5 to 10, or from 0.75 to 15, or from 0.75 to 12, or from 0.75 to 10, or from 1.0 to 10, or from 1.0 to 8.0, or from 1.0 to 5, or from 1.0 to 3 branches per thousand carbon atoms (SCB1/1000 Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc. The number of short chain branches in the first ethylene copolymer is determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the disclosure, the comonomer content in the first ethylene copolymer is substantially similar or approximately equal (e.g., within about ±0.01 mol %) to the comonomer content of the second ethylene copolymer (as reported for example in mol %).

In an embodiment of the disclosure, the comonomer content in the first ethylene copolymer is greater than comonomer content of the second ethylene copolymer (as reported for example in mol %).

In an embodiment of the disclosure, the amount of short chain branching in the first ethylene copolymer is substantially similar or approximately equal (e.g., within about ±0.05 SCB/1000 Cs) to the amount of short chain branching in the second ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000 Cs).

In an embodiment of the disclosure, the amount of short chain branching in the first ethylene copolymer is greater than the amount of short chain branching in the second ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000 Cs).

In an embodiment of the disclosure, the melt index, I₂ of the first ethylene copolymer is less than 0.4 g/10 min. The melt index of the first ethylene copolymer can in an embodiment of the disclosure be above 0.01, but below 0.4 g/10 min. In further embodiments of the disclosure, the melt index, I₂ of the first ethylene copolymer will be from 0.01 to 0.40 g/10 min, or from 0.01 to 0.30 g/10 min, or from 0.01 to 0.25 g/10 min, or from 0.01 to 0.20 g/10 min, or from 0.01 to 0.10 g/10 min.

In an embodiment of the disclosure, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 110,000 to about 300,000 (g/mol). In another embodiment of the disclosure, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 110,000 to about 275,000 or from about 110,000 to about 250,000. In another embodiment of the disclosure, the first ethylene copolymer has a weight average molecular weight M_(w) of greater than about 110,000 to less than about 250,000. In further embodiments of the disclosure, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 125,000 to about 225,000, or from about 135,000 to about 200,000. In embodiments of the disclosure, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 125,000 to about 275,000, or from about 125,000 to about 250,000, or from about 150,000 to about 275,000, or from about 150,000 to about 250,000, or from about 175,000 to about 250,000. In embodiments of the disclosure, the first ethylene copolymer has a M_(w) of greater than 110,000, or greater than 125,000, or greater than 150,000, or greater than 175,000. In embodiments of the disclosure the first ethylene copolymer has a M_(w) of greater than 110,000, or greater than 125,000, or greater than 150,000, or greater than 175,000 while at the same time being lower than 275,000, or 250,000.

In embodiments of the disclosure, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 125,000 to about 275,000, or from about 125,000 to about 250,000, or from 125,000 to about 230,000, or from about 150,000 to about 275,000, or from about 150,000 to about 250,000, or from about 175,000 to about 250,000, or from about 180,000 to about 230,000. In embodiments of the disclosure, the first ethylene copolymer has a M_(w) of greater than 150,000, or greater than 175,000, or greater than 180,000, or greater than 190,000, or greater than 200,000. In embodiments of the disclosure the first ethylene copolymer has a M_(w) of greater than 150,000, or greater than 175,000, or greater than 180,000, or greater than 190,000, or greater than 200,000 while at the same time being lower than 275,000, or 250,000.

In embodiments of the disclosure, the density of the first ethylene copolymer is from 0.920 to 0.955 g/cm³ or can be a narrower range within this range. For example, in further embodiments of the disclosure, the density of the first ethylene copolymer can be from 0.925 to 0.955 g/cm³, or from 0.925 to 0.950 g/cm³, or from 0.925 to 0.945 g/cm³, or from 0.925 to 0.940 g/cm³, or from 0.925 to 0.935 g/cm³, or from 0.923 to 0.945 g/cm³, or from 0.923 to 0.940 g/cm³, or from 0.923 to 0.935 g/cm³, or from 0.927 to 0.945 g/cm³, or from 0.927 to 0.940 g/cm³, or from 0.927 to 0.935 g/cm³, or from 0.920 to 0.940 g/cm³, or from 0.922 to 0.948 g/cm³, or from 0.925 to 0.935 g/cm³.

In an embodiments of the disclosure, the first ethylene copolymer has a molecular weight distribution M_(w)/M_(n) of <3.0, or ≤2.7, or <2.7, or ≤2.5, or <2.5, or ≤2.3, or from 1.8 to 2.3.

The Mw/M_(n) value of the first ethylene copolymer can in an embodiment of the disclosure be estimated by a de-convolution of a GPC profile obtained for a bimodal polyethylene composition of which the first ethylene copolymer is a component.

The density and the melt index, I₂, of the first ethylene copolymer can be estimated from GPC (gel permeation chromatography) and GPC-FTIR (gel permeation chromatography with Fourier transform infra-red detection) experiments and deconvolutions carried out on the bimodal polyethylene composition (see the Examples section).

In an embodiment of the disclosure, the first ethylene copolymer of the bimodal polyethylene composition is a homogeneously branched ethylene copolymer having a weight average molecular weight, Mw, of at least 110,000; a molecular weight distribution, M_(w)/M_(n), of less than 2.7 and a density of from 0.920 to 0.948 g/cm³.

In an embodiment of the disclosure, the first ethylene copolymer of the bimodal polyethylene composition is a homogeneously branched ethylene copolymer having a weight average molecular weight, Mw, of at least 175,000; a molecular weight distribution, M_(w)/M_(n), of less than 2.7 and a density of from 0.922 to 0.948 g/cm³.

In an embodiment of the present disclosure, the first ethylene copolymer is homogeneously branched ethylene copolymer and has a CDBI₅₀ of greater than about 50%, or greater than about 55% by weight. In further embodiments of the disclosure, the first ethylene copolymer has a CDBI₅₀ of greater than about 60%, or greater than about 65%, or greater than about 70%, or greater than about 75%, or greater than about 80% by weight.

In an embodiment of the disclosure, the first ethylene copolymer can comprise from 10 to 70 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the disclosure, the first ethylene copolymer comprises from 20 to 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the disclosure, the first ethylene copolymer comprises from 30 to 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the disclosure, the first ethylene copolymer comprises from 40 to 50 weight percent (wt %) of the total weight of the first and second ethylene copolymers.

The Second Ethylene Copolymer

In an embodiment of the disclosure, the second ethylene copolymer of the bimodal polyethylene composition has a density below 0.967 g/cm³ but which is higher than the density of the first ethylene copolymer; a melt index, I₂, of from about 100 to 10,000 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 3.0 and a weight average molecular weight M_(w) that is less than the M_(w) of the first ethylene copolymer. In an embodiment of the disclosure, the weight average molecular weight, M_(w) of the second ethylene copolymer will be below 45,000.

In an embodiment of the disclosure, the second ethylene copolymer of the bimodal polyethylene composition has a density below 0.967 g/cm³ but which is higher than the density of the first ethylene copolymer; a melt index, I₂, of from about 500 to about 20,000 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 2.7, and a weight average molecular weight M_(w) that is less than the M_(w) of the first ethylene copolymer.

In an embodiment of the disclosure, the second ethylene copolymer of the bimodal polyethylene composition has a density below 0.965 g/cm³ but which is higher than the density of the first ethylene copolymer; a melt index, I₂, of from about 250 to 20,000 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 2.7 and a weight average molecular weight M_(w) that is less than the M_(w) of the first ethylene copolymer.

In an embodiment of the disclosure, the second ethylene copolymer is homogeneously branched copolymer.

In an embodiment of the disclosure, the second ethylene copolymer is made with a single site catalyst, such as for example a phosphinimine catalyst.

In an embodiment of the disclosure, the comonomer content in the second ethylene copolymer can be from about 0.05 to about 3 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods. The comonomer content of the second ethylene polymer can also be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the disclosure, the comonomer content in the second ethylene copolymer can be from about 0.01 to about 3 mol %, or from about 0.03 to about 3 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods. The comonomer content of the second ethylene polymer can also be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the disclosure, the comonomer content in the second ethylene copolymer can be from about 0.01 to about 3 mol % or from about 0.03 to about 3 mol %, or from about 0.05 to about 3 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods. The comonomer content of the second ethylene polymer may be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the disclosure, the comonomer in the second ethylene copolymer is one or more alpha olefin such as but not limited to 1-butene, 1-hexene, 1-octene and the like.

In an embodiment of the disclosure, the second ethylene copolymer is a copolymer of ethylene and 1-octene.

In an embodiment of the disclosure, the short chain branching in the second ethylene copolymer can be from about 0.25 to about 15 short chain branches per thousand carbon atoms (SCB2/1000 Cs). In further embodiments of the disclosure, the short chain branching in the second ethylene copolymer can be from 0.25 to 12, or from 0.25 to 8, or from 0.25 to 5, or from 0.25 to 3, or from 0.25 to 2 branches per thousand carbon atoms (SCB2/1000 Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc. The number of short chain branches in the second ethylene copolymer can be measured by ¹³C NMR, or FTIR or GPC-FTIR methods. Alternatively, the number of short chain branches in the second ethylene copolymer can be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section). The comonomer is one or more suitable alpha olefin such as but not limited to 1-butene, 1-hexene, 1-octene and the like. IN one embodiment, the comonomer 1-octene is preferred.

In an embodiment of the disclosure, the short chain branching in the second ethylene copolymer can be from about 0.05 to about 12 short chain branches per thousand carbon atoms (SCB1/1000 Cs). In further embodiments of the disclosure, the short chain branching in the second ethylene copolymer can be from 0.05 to 7.5, or from 0.05 to 5.0, or from 0.05 to 2.5, or from 0.05 to 1.5, or from 0.1 to 12, or from 0.1 to 10, or from 0.1 to 7.5, or from 0.1 to 5.0, or from 0.1 to 2.5, or from 0.1 to 2.0, or from 0.1 to 1.0 branches per thousand carbon atoms (SCB1/1000 Cs).

In an embodiment of the disclosure, the short chain branching in the second ethylene copolymer can be from about 0.15 to about 15 short chain branches per thousand carbon atoms (SCB2/1000 Cs). In further embodiments of the disclosure, the short chain branching in the second ethylene copolymer can be from 0.15 to 12, or from 0.15 to 8, or from 0.15 to 5, or from 0.15 to 3, or from 0.15 to 2 branches per thousand carbon atoms (SCB2/1000 Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc.

The number of short chain branches in the second ethylene copolymer may be determined by mathematical deconvolution methods applied to a bimodal polyethylene composition (see the Examples section).

In an embodiment of the disclosure, the short chain branching in the second ethylene copolymer can be from about 0.05 to about 10 short chain branches per thousand carbon atoms (SCB1/1000 Cs). In further embodiments of the disclosure, the short chain branching in the second copolymer can be from 0.05 to 7.5, or from 0.05 to 5.0, or from 0.05 to 2.5, or from 0.05 to 1.5, or from 0.1 to 12, or from 0.1 to 10, or from 0.1 to 7.5, or from 0.1 to 5.0, or from 0.1 to 2.5, or from 0.1 to 2.0, or from 0.1 to 1.0 branches per thousand carbon atoms (SCB1/1000 Cs).

In an embodiment of the disclosure, the comonomer content in the second ethylene copolymer is substantially similar or approximately equal (e.g. within about ±0.01 mol %) to the comonomer content of the first ethylene copolymer (as reported for example in mol %).

In an embodiment of the disclosure, the comonomer content in the second ethylene copolymer is less than the comonomer content of the first ethylene copolymer (as reported for example in mol %).

In an embodiment of the disclosure, the amount of short chain branching in the second ethylene copolymer is substantially similar or approximately equal (e.g., within about ±0.05 SCB/1000 C) to the amount of short chain branching in the first ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000 Cs).

In an embodiment of the disclosure, the amount of short chain branching in the second ethylene copolymer is less than the amount of short chain branching in the first ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000 Cs).

In an embodiment of the present disclosure, the density of the second ethylene copolymer is less than 0.967 g/cm³. The density of the second ethylene copolymer in another embodiment of the disclosure is less than 0.966 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is less than 0.965 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is less than 0.964 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is less than 0.963 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is less than 0.962 g/cm³.

In an embodiment of the present disclosure, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.967 g/cm³. The density of the second ethylene copolymer in another embodiment of the disclosure is higher than the density of the first ethylene copolymer, but is less than 0.966 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.965 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.964 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.963 g/cm³. In another embodiment of the disclosure, the density of the second ethylene copolymer is higher than the density of the first ethylene copolymer, but is less than 0.962 g/cm³.

In an embodiment of the disclosure, the density of the second ethylene copolymer is from 0.952 to 0.967 g/cm³ or can be a narrower range within this range. For example, the density of the second ethylene copolymer may in embodiments of the disclosure be from 0.952 to 0.966 g/cm³, 0.952 to 0.965 g/cm³, or from 0.952 to 0.964 g/cm³, or from 0.952 to 0.963 g/cm³, or from 0.954 to 0.963 g/cm³, or from 0.954 to 0.964 g/cm³, or from 0.956 to 0.964 g/cm³, or from 0.956 to 0.963 g/cm³, or from 0.952 to less than 0.965 g/cm³, or from 0.954 to less than 0.965 g/cm³.

In an embodiment of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of less than 25,000. In another embodiment of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 7,500 to about 23,000. In further embodiments of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 9,000 to about 22,000, or from about 10,000 to about 17,500, or from about 7,500 to about 17,500. In still further embodiments of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 3,500 to about 25,000, or from about 5,000 to about 20,000, or from about 7,500 to about 17,500, or from about 5,000 to about 15,000, or from about 5,000 to about 17,500, or from about 7,500 to about 15,000 or from about 7,500 to about 12,500. In further embodiments of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 9,000 to about 22,000, or from about 10,000 to about 17,500, or from about 7,500 to 17,500.

In embodiments of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of less than about 45,000, or less than about 40,000 or less than about 35,000. In another embodiment of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 7,500 to about 35,000. In further embodiments of the disclosure, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 9,000 to about 35,000, or from about 10,000 to about 35,000, or from about 12,500 to about 30,000, or from about 10,000 to about 25,000, or from about 10,000 to about 20,000.

In embodiments of the disclosure, the second ethylene copolymer has a molecular weight distribution, M_(w)/M_(n) of <3.0, or ≤2.7, or <2.7, or ≤2.5, or <2.5, or ≤2.3, or from 1.8 to 2.3.

The Mw/Mn value of the second ethylene copolymer can in an embodiment of the disclosure be estimated by a de-convolution of a GPC profile obtained for a bimodal polyethylene composition of which the first ethylene copolymer is a component.

In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 20 to 10,000 g/10 min. In another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 100 to 10,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1,000 to 7,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1,200 to 10,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1,500 to 10,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be greater than 1,500, but less than 7,000 g/10 min.

In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 250 to 20,000 g/10 min. In another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 500 to 20,000 g/10 min. In another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from greater than 750 to 20,000 g/10 min. In further embodiments of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1000 to 20,000 g/10 min, or from 1,500 to 20,000 g/10 min, or from 250 to 15,000 g/10 min, or from 250 to 10,000 g/10 min or from 500 to 17,500 g/10 min, or from 500 to 15,000 g/10 min, or from 1,500 to 15,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1200 to 10,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1500 to 10,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be greater than 1500, but less than 7000 g/10 min.

In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 50 to 20,000 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 100 to 20,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 250 to 20,000 g/10 min.

In another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 500 to 20,000 g/10 min. In another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1000 to 20,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1500 to 20,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1500 to 10,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be from 1500 to 7,000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be greater than 1500, but less than 7000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be greater than 1500, but less than 5000 g/10 min. In yet another embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer can be greater than 1000, but less than 3500 g/10 min.

In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 200 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 250 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 500 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 650 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 1000 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 1200 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 1500 g/10 min. In an embodiment of the disclosure, the melt index I₂ of the second ethylene copolymer is greater than 1750 g/10 min.

The density and the melt index, I₂, of the second ethylene copolymer can be estimated from GPC and GPC-FTIR experiments and deconvolutions carried out on a bimodal polyethylene composition (see the below Examples section).

In an embodiment of the disclosure, the second ethylene copolymer of the polyethylene composition is a homogeneous ethylene copolymer having a weight average molecular weight, Mw, of at most 45,000; a molecular weight distribution, M_(w)/M_(n), of less than 2.7 and a density higher than the density of said first ethylene copolymer, but less than 0.967 g/cm³.

In an embodiment of the disclosure, the second ethylene copolymer of the bimodal polyethylene composition is a homogeneous ethylene copolymer having a weight average molecular weight, Mw, of at most 45,000; a molecular weight distribution, M_(w)/M_(n), of less than 2.7 and a density higher than the density of the first ethylene copolymer, but less than 0.965 g/cm³.

In an embodiment of the present disclosure, the second ethylene copolymer is homogeneously branched ethylene copolymer and has a CDBI₅₀ of greater than about 50 weight %, or for example, of greater than about 55 weight %. In further embodiments of the disclosure, the second ethylene copolymer has a CDBI₅₀ of greater than about 60 weight %, or greater than about 65 weight %, or greater than about 70 weight %, or greater than about 75 weight %, or greater than about 80 weight %.

In an embodiment of the disclosure, the second ethylene copolymer can comprise from 90 to 30 weight % (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the disclosure, the second ethylene copolymer comprises from 80 to 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the disclosure, the second ethylene copolymer comprises from 70 to 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the disclosure, the second ethylene copolymer comprises from 60 to 50 wt % of the total weight of the first and second ethylene copolymers.

In an embodiment of the present disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.037 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.036 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.035 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.034 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.033 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.032 g/cm³ higher than the density of the first ethylene copolymer. In another embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.031 g/cm³ higher than the density of the first ethylene copolymer. In still another embodiment of the disclosure, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.030 g/cm³ higher than the density of the first ethylene copolymer.

In embodiments of the disclosure, the 12 of the second ethylene copolymer is at least 100 times, or at least 1,000 times, or at least 10,000, or at least 50,000 times the 12 of the first ethylene copolymer.

The Bimodal Polyethylene Composition

In an embodiment of the disclosure, the bimodal polyethylene composition will contain a first ethylene copolymer and a second ethylene copolymer (as defined above) which are of different weight average molecular weight (M_(w)) and/or melt index, I₂.

In an embodiment of the disclosure, the bimodal polyethylene composition will minimally comprise a first ethylene copolymer and a second ethylene copolymer (as defined above) and the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (i.e., SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (i.e., SCB2) will be greater than 0.5 (i.e., SCB1/SCB2>0.5).

In an embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 0.60. In an embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 0.75. In another embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.0. In another embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at greater than 1.0. In yet another embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.25. In still further embodiments of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.5, or at least 1.75, or at least 2.0, or at least 2.5, or at least 3.0, or at least 3.5, or at least 4.0 or at least 4.5.

In an embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be greater than 0.5, but less than 1.0.

In embodiments of the disclosure, the ratio (SCB1/SCB2) of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be from 1.0 to 12.0, or from 1.0 to 10, or from 1.0 to 7.0, or from 1.0 to 5.0, or from 1.0 to 3.0.

In embodiments of the disclosure, the ratio (SCB1/SCB2) of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be from 1.0 to 15.0, or from 2.0 to 12.0, or from 2.5 to 12.0, or from 3.0 to 12.0, or from 3.5 to 12.0.

In an embodiment of the disclosure, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be from greater than 1.0 to about 5.0, or from greater than 1.0 to about 4.0, or from greater than 1.0 to about 3.5.

In an embodiment of the disclosure, the bimodal polyethylene composition has a bimodal molecular weight distribution. In the current disclosure, the term “bimodal” means that the polyethylene composition comprises at least two components, one of which has a lower weight average molecular weight and a higher density and another of which has a higher weight average molecular weight and a lower density. Typically, a bimodal or multimodal polyethylene composition can be identified by using gel permeation chromatography (GPC). Generally, the GPC chromatograph will exhibit two or more component ethylene copolymers, where the number of component ethylene copolymers corresponds to the number of discernible peaks. One or more component ethylene copolymers may also exist as a hump, shoulder or tail relative to the molecular weight distribution of the other ethylene copolymer component.

In an embodiment of the disclosure, the bimodal polyethylene composition has a density of greater than or equal to 0.949 g/cm³, as measured according to ASTM D792; a melt index, I₂, of from about 0.2 to about 3.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 3 to about 13, a Z-average molecular weight, M_(z) of less than 500,000, a stress exponent of less than 1.53 and an ESCR Condition B at 10% IGEPAL of at least 20 hours.

In an embodiment of the disclosure, the bimodal polyethylene composition has a density of greater of from about 0.949 g/cm³ to about 0.960 g/cm³ as measured according to ASTM D792; a melt index, I₂, of from about 0.2 to about 3.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 3 to about 13, a Z-average molecular weight, M_(z) of less than 500,000, a stress exponent of less than 1.53 and an ESCR Condition B at 10% IGEPAL of at least 20 hours.

In an embodiment of the disclosure, the bimodal polyethylene composition has a density of greater than or equal to 0.949 g/cm³, as measured according to ASTM D792; a melt index, I₂, of from about 0.4 to about 5.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 3 to about 11, a Z-average molecular weight, M_(z) of less than 400,000, a stress exponent of less than 1.50 and an ESCR Condition B at 10% IGEPAL of at least 20 hours.

In an embodiment of the disclosure, the bimodal polyethylene composition of the current disclosure has a density of greater than or equal to 0.949 g/cm³, as measured according to ASTM D792; a melt index, I₂, of from about 0.2 to about 5.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 6 to about 13, a Z-average molecular weight, M_(z) of less than 450,000, a stress exponent of less than 1.50 and an ESCR Condition B at 10% IGEPAL of at least 200 hours.

In an embodiment of the disclosure, the bimodal polyethylene composition has a density of greater than or equal to 0.949 g/cm³, as measured according to ASTM D792; a melt index, I₂, of from about 0.3 to about 4.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 5.0 to about 13.0, a Z-average molecular weight, M_(z) of from 400,000 to 520,000, a stress exponent of less than 1.53 and an environmental stress crack resistance, ESCR Condition B at 10% IGEPAL of at least 120 hours.

In embodiments of the disclosure, the bimodal polyethylene composition has a comonomer content of less than 0.75 mol %, or less than 0.70 mol %, or less than 0.65 mol %, or less than 0.60 mol %, or less than 0.55 mol % as measured by FTIR or ¹³C NMR methods, with ¹³C NMR being preferred, where the comonomer is one or more suitable alpha olefins such as but not limited to 1-butene, 1-hexene, 1-octene and the like. In an embodiment of the disclosure, the bimodal polyethylene composition has a comonomer content of from 0.1 to 0.75 mol %, or from 0.20 to 0.55 mol %, or from 0.25 to 0.50 mol %.

In the present disclosure, the bimodal polyethylene composition has a density of at least 0.949 g/cm³. In further embodiments of the disclosure, the bimodal polyethylene composition has a density of >0.949 g/cm³, or ≥0.950 g/cm³, or >0.950 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.964 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.962 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.960 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.959 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.958 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.957 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.956 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.949 to 0.955 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.950 to 0.955 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.951 to 0.960 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.951 to 0.957 g/cm³.

In an embodiment of the current disclosure, the bimodal polyethylene composition has a density in the range of from 0.951 to 0.955 g/cm³.

In an embodiment of the disclosure, the bimodal polyethylene composition has a melt index, I₂, of between 0.4 and 5.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight) and including narrower ranges within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a melt index, I₂, of from 0.5 to 5.0 g/10 min, or from 0.4 to 3.5 g/10 min, or from 0.4 to 3.0 g/10 min, or from 0.4 to 2.5 g/10 min, or from 0.4 to 2.0 g/10 min, or from 0.5 to 3.5 g/10 min, or from 0.5 to 3.0 g/10 min, or from 1.0 to 3.0 g/10 min, or from about 1.0 to about 2.0 g/10 min, or from more than 0.5 to less than 2.0 g10/min.

In an embodiment of the disclosure, the bimodal polyethylene composition has a melt index, I₂, of between 0.1 and 5.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight) and including narrower ranges within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a melt index, I₂, of from 0.2 to 5.0 g/10 min, or from 0.3 to 4.0 g/10 min, or from 0.3 to 3.5 g/10 min, or from 0.3 to 3.0 g/10 min, or from 0.2 to 3.5 g/10 min, or from 0.2 to 3.0 g/10 min, or from 0.1 to 2.5 g/10 min, or from 0.1 to 2.0 g/10 min.

In an embodiment of the disclosure, the bimodal polyethylene composition has a melt index, I₂, of from 0.1 to 5.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight) including narrower ranges within this range and all the numbers within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a melt index, I₂, of from 0.2 to 5.0 g/10 min, or from 0.3 to 4.0 g/10 min, or from 0.4 to 3.5 g/10 min, or from 0.4 to 3.0 g/10 min, or from 0.3 to 3.5 g/10 min, or from 0.3 to 3.0 g/10 min, or from 0.3 to 2.5 g/10 min, or from 0.1 to 4.0 g/10 min, or from 0.1 to 3.5 g/10 min, or from 0.1 to 3.0 g/10 min, or from 0.1 to 2.5 g/10 min, or from 0.1 to 2.0 g/10 min, or from 0.1 to 1.5 g/10 min, or from 0.25 to 1.5 g/10 min, or from 0.3 to 2.0 g/10 min, or from 0.3 to 1.5 g/10 min, or less than 1.0 g/10 min, or from greater than 0.1 to less than 1.0 g/10 min, or from greater than 0.2 to less than 1.0 g/10 min, or from greater than 0.3 to less than 1.0 g/10 min.

In an embodiment of the disclosure, the bimodal polyethylene composition has a melt index I₅ of at least 1.0 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 5 kg weight). In another embodiment of the disclosure, the bimodal polyethylene composition has a melt index, I₅, of greater than about 1.1 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 5 kg weight). In still further embodiments of the disclosure, the bimodal polyethylene composition has a melt index I₅ of from about 1.0 to about 10.0 g/10 min, or from about 2.0 to about 8.0 g/10 min, or from about 1.0 to about 5.0 g/10 min, or from about 1.5 to about 6.5 g/10 min, or from about 4.0 to about 7.0 g/10 min, or from about 3.0 to about 6.5 g/10 min. In yet still further embodiments of the disclosure, the bimodal polyethylene composition has a melt index I₅ of from about 1.0 to about 5.0 g/10 min, or from about 1.5 to about 5.0 g/10 min, or from about 2.0 to about 5.0 g/10 min, or from about 2.0 to about 4.5 g/10 min.

In an embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁ of at least 25 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 21 kg weight). In another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 30 g/10 min. In yet another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 35 g/10 min. In still another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 40 g/10 min. In still another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 50 g/10 min. In still another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 60 g/10 min. In yet another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 65 g/10 min. In still another embodiment of the disclosure, the bimodal polyethylene composition has a high load melt index, I₂₁, of greater than about 75 g/10 min.

In an embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the bimodal polyethylene composition is from 200 to 1,500. In an embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, Is, of the bimodal polyethylene composition is from 200 to 2000. In another embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the bimodal polyethylene composition is from 400 to 1300. In yet another embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the bimodal polyethylene composition is from 600 to 1,200.

In an embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, Is, of the bimodal polyethylene composition is from 500 to 5,000. In another embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the bimodal polyethylene composition is from 750 to 4,500. In yet another embodiment of the disclosure, the ratio of the melt index, I₂, of the second ethylene copolymer to the melt index, I₅, of the bimodal polyethylene composition is from 1,000 to 4,000.

In an embodiment of the disclosure, the bimodal polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere between from about 1 to about 10 kPa which is between 1,000 to 25,000 Pa·s. In an embodiment of the disclosure, the bimodal polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere from about 1 to about 10 kPa which is between 1,000 to 10,000 Pa·s.

In an embodiment of the disclosure, the bimodal polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere between from about 1 to about 10 kPa which is between 1,000 to 25,000 Pa·s. In an embodiment of the disclosure, the bimodal polyethylene composition has a complex viscosity, η* at a shear stress (G*) anywhere from about 1 to about 10 kPa which is from 1,000 to 10,000 Pa·s, or from 1,000 to 15,000 Pa·s, or from 3,000 to 12,500 Pa·s, or from 1,000 to 15,000, or from 5000 to 15,000 Pa·s.

In an embodiment of the disclosure, the bimodal polyethylene composition has a number average molecular weight, M_(n), of below about 30,000. In another embodiment of the disclosure, the bimodal polyethylene composition has a number average molecular weight, M_(n), of below about 20,000 or below about 17,500. In further embodiments of the disclosure, the bimodal polyethylene composition has a number average molecular weight, M_(n), of from about 5,000 to 25,000, or from about 5,000 to 20,000, or from about 7,000 to about 15,000. In further embodiments of the disclosure, the bimodal polyethylene composition has a number average molecular weight, M_(n), of from about 9,000 to 28,000, or from about 10,000 to 25,000, or from about 10,000 to about 20,000.

In embodiments of the disclosure, the bimodal polyethylene composition has a weight average molecular weight, M_(w), of from about 60,000 to about 200,000 including narrower ranges within this range and the numbers within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a weight average molecular weight, M_(w), of from about 65,000 to 175,000, or from about 65,000 to about 150,000, or from about 65,000 to about 140,000.

In embodiments of the disclosure, the bimodal polyethylene composition has a weight average molecular weight, M_(w), of from about 65,000 to about 200,000 including narrower ranges within this range and the numbers within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a weight average molecular weight, M_(w), of from about 75,000 to about 175,000, or from about 90,000 to about 150,000, or from about 100,000 to about 140,000.

In an embodiment of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(z), of less than 500,000. In another embodiment of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(z), of less than 450,000.

In embodiments of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(z) of from 250,000 to 450,000 including narrower ranges within this range and the numbers within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(w), of from 250,000 to 425,000, or from 275,000 to 425,000, or from 250,000 to below 450,000, or from 250,000 to 410,000.

In embodiments of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(z), of from 400,000 to 520,000 including narrower ranges within this range and the numbers within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(z), of from 400,000 to 510,000, or from 400,000 to 500,000, or from 400,000 to 490,000, or from 410,000 to 480,000.

In embodiments of the disclosure, the bimodal polyethylene composition has a z-average molecular weight, M_(z) which satisfies: 400,000<Mz<500,000 or 400,000 ≤Mz≤500,000.

In embodiments of the present disclosure, the bimodal polyethylene composition has a molecular weight distribution Mw/Mn of from 3.0 to 11.0 or a narrower range within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a M_(w)/M_(n) of from 4.0 to 10.0, or from 4.0 to 9.0 or from 5.0 to 10.0, or from 5.0 to 9.0, or from 4.5 to 10.0, or from 4.5 to 9.5, or from 4.5 to 9.0, or from 4.5 to 8.5, or from 5.0 to 8.5.

In embodiments of the present disclosure, the bimodal polyethylene composition has a molecular weight distribution Mw/Mn of from 6.0 to 13.0 or a narrower range within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a M_(w)/M_(n) of from 7.0 to 12.0, or from 8.0 to 12.0, or from 8.5 to 12.0, or from 9.0 to 12.0, or from 9.0, to 12.5 or from 8.5 to 12.5.

In embodiments of the present disclosure, the bimodal polyethylene composition has a molecular weight distribution Mw/Mn of from 3.0 to 13.0, including narrower ranges within this range and all the numbers within this range. For example, in further embodiments of the disclosure, the bimodal polyethylene composition has a M_(w)/M_(n) of from 5.0 to 13.0, or from 4.0 to 12.0, or from 5.0 to 12.0 or from 6.0 to 12.0, or from 6.0 to 11.0, or from 5.0 to 12.0, or from 5.0 to 10.0, or from 6.0 to 10.0, or from 6.0 to 11.0, or from 7.0 to 11.0, or from greater than 7.0 to 11.0, or from 7.0 to 10.0, or from greater than 7.0 to 12.0.

In embodiments of the disclosure, the bimodal polyethylene composition has a ratio of Z-average molecular weight to weight average molecular weight (M_(z)/M_(w)) of from 2.0 to 5.0, or from 2.25 to 5.0, or from 2.75 to 5.0, or from 2.75 to 4.25, or from 3.0 to 4.0, or from 2.25 to 4.75, or from 2.25 to 4.5, or from 2.5 to 4.5, or from 2.5 to 4.25, or from 2.75 to 4.0, or from 2.75 to 3.75, or between 3.0 and 4.0.

In embodiments of the disclosure, the bimodal polyethylene composition has a ratio of Z-average molecular weight to weight average molecular weight (M_(z)/M_(w)) of less than 5.0, or less than 4.5, or less than 4.0, or less than 3.5.

In an embodiment of the disclosure, the bimodal polyethylene composition has a broadness factor defined as (M_(w)/M_(n))/(M_(z)/M_(w)) of at least 2.70, or at least 2.75, or at least 2.8, or at least 2.85, or at least 2.90, or at least 2.95, or at least 3.00, or at least 3.05.

In an embodiment of the disclosure, the bimodal polyethylene composition has a broadness factor defined as (M_(w)/M_(n))/(M_(z)/M_(w)) of less than 3.00, or less than 2.95, or less than 2.90, or less than 2.85, or less than 2.80, or less than 2.75, or less than 2.70, or less than 2.65, or less than 2.60, or less than 2.55, or less than 2.50, or less than 2.45, or less than 2.40, or less than 2.35, or ≤2.75, or ≤2.70, or ≤2.65, or ≤2.60, or ≤2.55, or ≤2.50, or ≤2.45, or ≤2.40, or ≤2.35.

In embodiments of the disclosure, the bimodal polyethylene composition has a melt flow ratio defined as I₂₁/I₂ of >40, or ≥45, or ≥50, or ≤60, or ≥65. In a further embodiment of the disclosure, the bimodal polyethylene composition has a melt flow ratio I₂₁/I₂ of from about 40 to about 100, and including narrower ranges within this range. For example, the bimodal polyethylene composition may have a melt flow ratio I₂₁/I₂ of from about 45 to about 90, or from about 45 to about 80, or from about 45 to about 75, or from about 45 to about 70, or from about 50 to about 90, or from about 50 to about 80, or from about 50 to about 75, or from about 50 to about 70.

In embodiments of the disclosure, the bimodal polyethylene composition has a melt flow ratio defined as I₂₁/I₂ of >40, or ≥45, or ≥50, or ≥55, or ≥60, or ≥65, or ≥70. In a further embodiment of the disclosure, the bimodal polyethylene composition has a melt flow ratio I₂₁/I₂ of from about 40 to about 120, including narrower ranges within this range and all the numbers within this range. For example, the bimodal polyethylene composition may have a melt flow ratio I₂₁/I₂ of from about 50 to about 120, or from about 40 to about 110, or from about 45 to about 100, or from about 50 to about 110, or from about 55 to about 95.

In an embodiment of the disclosure, the bimodal polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 35. In an embodiment of the disclosure, the bimodal polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 30. In another embodiment of the disclosure, the bimodal polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 25. In another embodiment of the disclosure, the bimodal polyethylene composition has a melt flow rate defined as I₂₁/I₅ of less than 20.

In an embodiment of the disclosure, the bimodal polyethylene composition has a shear viscosity at about 10⁵ s⁻¹ (240° C.) of less than about 10 (Pa·s). In further embodiments of the disclosure, the bimodal polyethylene composition has a shear viscosity at about 10⁵ s⁻¹ (240° C.) of less than 7.5 Pa·s, or less than 6.0 Pa·s. In further embodiments of the disclosure, the bimodal polyethylene composition has a shear viscosity of less than 7.0 Pa·s, or less than 6.5 Pa·s.

In an embodiment of the disclosure, the bimodal polyethylene composition has a hexane extractables level of below 0.55 wt %.

In an embodiment of the disclosure, the bimodal polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than 0.75 mol % as determined by ¹³C NMR. In an embodiment of the disclosure, the bimodal polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than 0.65 mol % as determined by ¹³C NMR. In an embodiment of the disclosure, the bimodal polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than 0.55 mol % as determined by ¹³C NMR.

In an embodiment of the disclosure, the shear viscosity ratio, SVR_((10,1000)) at 240° C. of the bimodal polyethylene composition can be from about 4.0 to 25, or from 4.0 to 20, or from 4.0 to 17. The shear viscosity ratio SVR_((10,1000)) is determined by taking the ratio of shear viscosity at shear rate of 10 s⁻¹ and shear viscosity at shear rate of 1000 s⁻¹ as measured with a capillary rheometer at constant temperature (e.g. 240° C.), and a die with L/D ratio of 20 and diameter of 0.06″. Without wishing to be bound by theory, the higher the value for the shear viscosity ratio, the easier the bimodal polyethylene composition is to be processed on a converting equipment for caps and closures.

In an embodiment of the disclosure, the shear viscosity ratio, SVR_((10,1000)) at 240° C. of the bimodal polyethylene composition can be from about 10 to 30, or from 12 to 27, or from 12.5 to 25, or from 15 to 25, or from 17.5 to 23.0. The shear viscosity ratio SVR_((10,1000)) is determined by taking the ratio of shear viscosity at shear rate of 10 s⁻¹ and shear viscosity at shear rate of 1000 s⁻¹ as measured with a capillary rheometer at a constant temperature (e.g., 240° C.), and a die with L/D ratio of 20 and diameter of 0.06″. Without wishing to be bound by theory, the higher the value for the shear viscosity ratio, the easier the bimodal polyethylene composition is to be processed on converting equipment for caps and closures. The “shear viscosity ratio” is used herein as a means to describe the relative processability of a bimodal polyethylene composition.

In embodiments of the disclosure, the bimodal polyethylene composition has a shear viscosity ratio (_(η10/η1000) at 240° C.) of ≥12.0, ≥12.5, or ≥13.0, or ≥13.5, or ≥14.0, or ≥14.5, or ≥15.0, or ≥17.5, or ≥20.0. The “shear viscosity ratio” is used herein as a means to describe the relative processability of a bimodal polyethylene composition.

In further embodiments of the disclosure, the shear viscosity ratio, SVR_((10,1000)) at 240° C. of the bimodal polyethylene composition is from 10.0 to 30, or from 12.0 to 30, or from 12.0 to 27.5, or from 12.0 to 25, or from 12.5 to 30, or from 12.5 to 27.5, or from 12.5 to 25.

In an embodiment of the disclosure, the bimodal polyethylene composition has a shear viscosity ratio (_(η10/η1000) at 240° C.) of ≥12.0, ≥12.5, or ≥13.0, or ≥13.5, or ≥14.0, or ≥14.5, or ≥15.0, or ≥17.5, or ≥20.0.

In an embodiment of the disclosure, the shear thinning index, SHI_((1,100)) of the bimodal polyethylene composition is less than about 10; in another embodiment the SHI_((1,100)) will be less than about 7. The shear thinning index (SHI), was calculated using dynamic mechanical analysis (DMA) frequency sweep methods as disclosed in PCT applications WO 2006/048253 and WO 2006/048254. The SHI value is obtained by calculating the complex viscosities η*(1) and η* (100) at a constant shear stress of 1 kPa (G*) and 100 kPa (G*), respectively.

In an embodiment of the disclosure, the SHI_((1,100)) of the bimodal polyethylene composition satisfies the equation: SHI_((1,100))<−10.58 (log I₂ of bimodal polyethylene composition in g/10 min)/(g/10 min)+12.94. In another embodiment of the disclosure, the SHI_((1,100)) of the bimodal polyethylene composition satisfies the equation: SHI_((1,100))<−5.5(log I ₂ of the bimodal polyethylene composition in g/10 min)/(g/10 min)+9.66.

In an embodiment of the disclosure, the bimodal polyethylene composition has a Rosand melt strength in centiNewtons (cN) of at least 2.0, or at least 2.25, or at least 2.5, or at least 2.75, or at least 3.0, or at least 3.25, or at least 3.5, or at least 3.75, or from 2.5 to 6.0, or from 2.75 to 6.0, or from 2.75 to 5.5, or from 3.0 to 6.0, or from 3.0 to 5.5, or from 3.25 to 6.0, or from 3.5 to 6.0, or from 3.25 to 5.5.

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 20 hours, or at least 50 hours, or at least 60 hours, or at least 80 hours, or at least 120 hours, or at least 150 hours, or from 60 to 400 hours, or from 100 to 250 hours, or from 60 to 250 hours as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 100 hrs, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 150 hrs, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 200 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 250 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 300 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 350 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 400 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of at least 500 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 200 to 1500 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 200 to 1250 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 300 to 1500 hours, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 50 to 600 hrs, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 100 to 500 hrs, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition, has an environment stress crack resistance ESCR Condition B at 10% of from 150 to 500 hrs, as measured according to ASTM D1693 (at 10% Igepal and 50° C. under condition B).

In an embodiment of the disclosure, the bimodal polyethylene composition or a molded article (or plaque) made from the bimodal polyethylene composition has a notched Izod impact strength of at least 60 J/m, or at least 70 J/m, or at least 80 J/m, or at least 90 J/m, or at least 100 J/m as measured according to ASTM D256.

In an embodiment of the disclosure the bimodal polyethylene composition of the current disclosure has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.5 to 3.0 g/10 min; a molecular weight distribution of from 4.0 to 10.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 10 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m, and an ESCR B at 10% of at least 20 hours.

In an embodiment of the disclosure the bimodal polyethylene composition of the current disclosure has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.5 to 3.0 g/10 min; a molecular weight distribution of from 4.5 to 9.5; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 7 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m and an ESCR B at 10% of at least 80 hours.

In an embodiment of the disclosure the bimodal polyethylene composition of the current disclosure has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.2 to 3.0 g/10 min; a molecular weight distribution of from 6.0 to 13.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 10 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m, and an ESCR B at 10% of at least 200 hours.

In an embodiment of the disclosure the bimodal polyethylene composition of the current disclosure has a density of from 0.949 to 0.957 g/cm³; a melt index, I₂, of from 0.3 to 2.0 g/10 min; a molecular weight distribution of from 6.0 to 12.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 10 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m, and an ESCR B at 10% of at least 150 hrs.

In embodiments of the disclosure, the bimodal polyethylene composition has a 2% secant flexural modulus in megapascals (MPa) of greater than about 750, or greater than about 850, or greater than about 1000, or from about 750 to about 1600, or from about 750 to about 1250, or from about 850 to about 1150. In some embodiments the bimodal polyethylene composition further comprises a nucleating agent which increases the 2% secant flexural modulus in megapascals (MPa) to above these ranges to for example from more than about 1000 and up to about 1600. Without wishing to be bound by theory, the 2% secant flexural modulus is a measure of polymer stiffness. The higher the 2% secant flexural modulus, the higher the polymer stiffness.

In an embodiment of the disclosure the bimodal polyethylene composition of the current disclosure has a density of from 0.949 to 0.956 g/cm³; a melt index, I₂, of from 0.2 to 3.0 g/10 min; a molecular weight distribution of from 7.0 to 12.0; a number average molecular weight, M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 7 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 60 J/m and an ESCR B at 10% of at least 200 hours.

In an embodiment of the disclosure, the bimodal polyethylene composition has a stress exponent, defined as Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16], which is ≤1.53, or <1.53. In an embodiment of the disclosure, the bimodal polyethylene composition has a stress exponent, defined as Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16], which is 1.50. In further embodiments of the disclosure the bimodal polyethylene composition has a stress exponent, Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16] of less than 1.50, or less than 1.48, or less than 1.45, or less than 1.43, or less than 1.40.

In an embodiment of the disclosure, the bimodal polyethylene composition has a composition distribution breadth index (CDBI₅₀), as determined by temperature elution fractionation (TREF), of ≥60 weight %. In further embodiments of the disclosure, the bimodal polyethylene composition will have a CDBI₅₀ of greater than 65 weight %, or greater than 70 weight %, or greater than 75 weight %, or greater than 80 weight %.

In an embodiment of the disclosure, the bimodal polyethylene composition has a composition distribution breadth index (CDBI₂₅), as determined by temperature elution fractionation (TREF), of ≥50 weight %. In further embodiments of the disclosure, the bimodal polyethylene composition will have a CDBI₂₅ of greater than 55 weight %, or greater than 60 weight %, or greater than 65 weight %, or greater than 70 weight %.

Optionally, additives can be added to the bimodal polyethylene composition. Additives can be added to the bimodal polyethylene composition during an extrusion or compounding step, but other suitable known methods will be apparent to a person skilled in the art. The additives can be added as is or as part of a separate polymer component (i.e., not the first or second ethylene polymers described above) added during an extrusion or compounding step. Suitable additives are known in the art and include but are not-limited to antioxidants, phosphites and phosphonites, nitrones, antacids, UV light stabilizers, UV absorbers, metal deactivators, dyes, fillers and reinforcing agents, nano-scale organic or inorganic materials, antistatic agents, lubricating agents such as calcium stearates, slip additives such as erucamide, and nucleating agents (including nucleators, pigments or any other chemicals which may provide a nucleating effect to the bimodal polyethylene composition). The additives that can be optionally added are typically added in amount of up to 20 weight percent (wt %).

One or more nucleating agent(s) may be introduced into the bimodal polyethylene composition by kneading a mixture of the polymer, usually in powder or pellet form, with the nucleating agent, which may be utilized alone or in the form of a concentrate containing further additives such as stabilizers, pigments, antistatics, UV stabilizers and fillers. It should be a material which is wetted or absorbed by the polymer, which is insoluble in the polymer and of melting point higher than that of the polymer, and it should be homogeneously dispersible in the polymer melt in as fine a form as possible (1 to 10 μm). Compounds known to have a nucleating capacity for polyolefins include salts of aliphatic monobasic or dibasic acids or arylalkyl acids, such as sodium succinate or aluminum phenylacetate; and alkali metal or aluminum salts of aromatic or alicyclic carboxylic acids such as sodium 6-naphthoate. Another compound known to have nucleating capacity is sodium benzoate. The effectiveness of nucleation may be monitored microscopically by observation of the degree of reduction in size of the spherulites into which the crystallites are aggregated.

Examples of nucleating agents which are commercially available and which may be added to the bimodal polyethylene composition are dibenzylidene sorbital esters (such as the products sold under the trademark MILLAD® 3988 by Milliken Chemical and IRGACLEAR® by Ciba Specialty Chemicals). Further examples of nucleating agents which may added to the bimodal polyethylene composition include the cyclic organic structures disclosed in U.S. Pat. No. 5,981,636 (and salts thereof, such as disodium bicyclo [2.2.1] heptene dicarboxylate); the saturated versions of the structures disclosed in U.S. Pat. No. 5,981,636 (as disclosed in U.S. Pat. No. 6,465,551; Zhao et al., to Milliken); the salts of certain cyclic dicarboxylic acids having a hexahydrophthalic acid structure (or “HHPA” structure) as disclosed in U.S. Pat. No. 6,599,971 (Dotson et al., to Milliken); and phosphate esters, such as those disclosed in U.S. Pat. No. 5,342,868 and those sold under the trade names NA-11 and NA-21 by Asahi Denka Kogyo, cyclic dicarboxylates and the salts thereof, such as the divalent metal or metalloid salts, (particularly, calcium salts) of the HHPA structures disclosed in U.S. Pat. No. 6,599,971. For clarity, the HHPA structure generally comprises a ring structure with six carbon atoms in the ring and two carboxylic acid groups which are substituents on adjacent atoms of the ring structure. The other four carbon atoms in the ring may be substituted, as disclosed in U.S. Pat. No. 6,599,971. An example is 1,2-cyclohexanedi-carboxylicacid, calcium salt (CAS registry number 491589-22-1). Still further examples of nucleating agents which may added to the bimodal polyethylene composition include those disclosed in WO2015042561, WO2015042563, WO2015042562 and WO 2011050042.

Many of the above described nucleating agents may be difficult to mix with the bimodal polyethylene composition that is being nucleated and it is known to use dispersion aids, such as for example, zinc stearate, to mitigate this problem.

In an embodiment of the disclosure, the nucleating agents are well dispersed in the bimodal polyethylene composition.

In an embodiment of the disclosure, the amount of nucleating agent used is comparatively small (from 5 to 3000 parts by million per weight (based on the weight of the bimodal polyethylene composition)) so it will be appreciated by those skilled in the art that some care must be taken to ensure that the nucleating agent is well dispersed. In an embodiment of the disclosure, the nucleating agent is added in finely divided form (less than 50 microns, especially less than 10 microns) to the bimodal polyethylene composition to facilitate mixing. This type of “physical blend” (i.e., a mixture of the nucleating agent and the resin in solid form) is generally preferable to the use of a “masterbatch” of the nucleator (where the term “masterbatch” refers to the practice of first melt mixing the additive—the nucleator, in this case—with a small amount of the bimodal polyethylene composition resin—then melt mixing the “masterbatch” with the remaining bulk of the bimodal polyethylene composition resin).

In an embodiment of the disclosure, an additive such as nucleating agent may be added to the bimodal polyethylene composition by way of a “masterbatch”, where the term “masterbatch” refers to the practice of first melt mixing the additive (e.g., a nucleator) with a small amount of the bimodal polyethylene composition, followed by melt mixing the “masterbatch” with the remaining bulk of the bimodal polyethylene composition.

In an embodiment of the disclosure, the polymer composition further comprises a nucleating agent or a mixture of nucleating agents.

In an embodiment of the disclosure, the polymer compositions described above are used in the formation of molded articles. For example, articles formed by continuous compression molding and injection molding are contemplated. Such articles include, for example, caps, screw caps, and closures for bottles. However, a person skilled in the art will readily appreciate that the compositions described above may also be used for other applications such as, but not limited to, film, injection blow molding, blow molding and sheet extrusion applications.

The bimodal polyethylene composition of this disclosure can be made using any conventional blending method such as but not limited to physical blending and in-situ blending by polymerization in multi reactor systems. For example, it is possible to perform the mixing of the first ethylene copolymer with the second ethylene copolymer by molten mixing of the two preformed polymers. Preferred are processes in which the first and second ethylene copolymers are prepared in at least two sequential polymerization stages, however, both in-series and in-parallel reactor process are contemplated for use in the current disclosure. If the at least two reactors are configured in parallel, comonomer addition to each reactor makes an ethylene copolymer in each reactor. If the at least two reactors are configured in series, comonomer may be added to at least the first reactor, and unreacted comonomer can flow into later reactors to make an ethylene copolymer in each reactor. Alternatively, if the at least two reactors are configured in series, comonomer may be added to each reactor, to make an ethylene copolymer in each reactor. Gas phase, slurry phase or solution phase reactor systems may be used. In one embodiment, the solution phase reactor systems is preferred.

In an embodiment of the current disclosure, a dual reactor solution process is used as has been described in for example U.S. Pat. No. 6,372,864 and U.S. Patent Publication Application No. 20060247373A1 which are incorporated herein by reference.

Homogeneously branched ethylene copolymers can be prepared using any catalyst capable of producing homogeneous branching. Generally, the catalysts will be based on a group 4 metal having at least one cyclopentadienyl ligand that is well known in the art. Examples of such catalysts which include metallocenes, constrained geometry catalysts and phosphinimine catalysts are typically used in combination with activators selected from methylaluminoxanes, boranes or ionic borate salts and are further described in U.S. Pat. Nos. 3,645,992; 5,324,800; 5,064,802; 5,055,438; 6,689,847; 6,114,481 and 6,063,879. Such catalysts may also be referred to as “single site catalysts” to distinguish them from traditional Ziegler-Natta or Phillips catalysts which are also well known in the art. In general, single site catalysts produce ethylene copolymers having a molecular weight distribution (Mw/M_(n)) of less than about 3.0 and a composition distribution breadth index (CDBI₅₀) of greater than about 50% by weight.

In an embodiment of the current disclosure, homogeneously branched ethylene polymers are prepared using an organometallic complex of a group 3, 4 or 5 metal that is further characterized as having a phosphinimine ligand. Such catalysts are known generally as phosphinimine catalysts. Some non-limiting examples of phosphinimine catalysts can be found in U.S. Pat. Nos. 6,342,463; 6,235,672; 6,372,864; 6,984,695; 6,063,879; 6,777,509 and 6,277,931 all of which are incorporated by reference herein.

Some non-limiting examples of metallocene catalysts can be found in U.S. Pat. Nos. 4,808,561; 4,701,432; 4,937,301; 5,324,800; 5,633,394; 4,935,397; 6,002,033 and 6,489,413, which are incorporated herein by reference. Some non-limiting examples of constrained geometry catalysts can be found in U.S. Pat. Nos. 5,057,475; 5,096,867; 5,064,802; 5,132,380; 5,703,187 and 6,034,021, all of which are incorporated by reference herein in their entirety.

In an embodiment of the disclosure, use of a single site catalyst that does not produce long chain branching (LCB) is preferred. Without wishing to be bound by any single theory, long chain branching can increase viscosity at low shear rates, thereby negatively impacting cycle times during the manufacture of caps and closures, such as during the process of compression molding. Long chain branching may be determined using ¹³C NMR methods and may be quantitatively assessed using the method disclosed by Randall in Rev. Macromol. Chem. Phys. C29 (2 and 3), p. 285.

In an embodiment of the disclosure, the bimodal polyethylene composition will contain fewer than 0.3 long chain branches per 1000 carbon atoms. In another embodiment of the disclosure, the bimodal polyethylene composition will contain fewer than 0.01 long chain branches per 1000 carbon atoms.

In an embodiment of the disclosure, the bimodal polyethylene composition (defined as above) is prepared by contacting ethylene and at least one alpha-olefin with a polymerization catalyst under solution phase polymerization conditions in at least two polymerization reactors (for an example of solution phase polymerization conditions see, for example, U.S. Pat. Nos. 6,372,864; 6,984,695 and U.S. Patent Publication Application No. 200610247373A1 which are incorporated herein by reference).

In an embodiment of the disclosure, the bimodal polyethylene composition is prepared by contacting at least one single site polymerization catalyst system (comprising at least one single site catalyst and at least one activator) with ethylene and a least one comonomer (e.g., a C3-C8 alpha-olefin) under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the disclosure, a group 4 single site catalyst system, comprising a single site catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of an alpha-olefin comonomer.

In an embodiment of the disclosure, a group 4 single site catalyst system, comprising a single site catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of 1-octene.

In an embodiment of the disclosure, a group 4 phosphinimine catalyst system, comprising a phosphinimine catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of an alpha-olefin comonomer.

In an embodiment of the disclosure, a group 4 phosphinimine catalyst system, comprising a phosphinimine catalyst and an activator, is used in a solution phase dual reactor system to prepare a bimodal polyethylene composition by polymerization of ethylene in the presence of 1-octene.

In an embodiment of the disclosure, a solution phase dual reactor system comprises two solution phase reactors connected in series.

In an embodiment of the disclosure, a polymerization process to prepare the bimodal polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the disclosure, a polymerization process to prepare the bimodal polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least a first reactor and a second reactor configured in series.

In an embodiment of the disclosure, a polymerization process to prepare the bimodal polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least a first reactor and a second reactor configured in series, with the at least one alpha-olefin comonomer being fed exclusively to the first reactor.

The production of the bimodal polyethylene composition of the present disclosure will typically include an extrusion or compounding step. Such steps are well known in the art.

The bimodal polyethylene composition can comprise further polymer components in addition to the first and second ethylene polymers. Such polymer components include polymers made in situ or polymers added to the polymer composition during an extrusion or compounding step.

In an embodiment of the disclosure, the polymer compositions described above are used in the formation of molded articles. For example, articles formed by continuous compression molding and injection molding are contemplated. Such articles include, for example, caps, screw caps, and closures for bottles.

In an embodiment of the disclosure, the closure made is a PCO 1881 CSD closure, having a weight of about 2.15 grams and having the following dimensions: Closure height (not including Tamper Ring)=about 10.7 mm; Closure height with Tamper Ring=about 15.4 mm; Outside diameter @ 4 mm=about 29.6 mm; Thread diameter=about 25.5 mm; Bump seal diameter=about 24.5 mm; Bump seal thickness=about 0.7 mm; Bump seal height to center of olive=about 1.5 mm; Bore seal diameter=about 22.5 mm; Bore seal thickness=about 0.9 mm; Bore height to center of olive=about 1.6 mm; Top panel thickness=about 1.2 mm; Tamper band undercut diameter=about 26.3 mm; Thread depth=about 1.1 mm; Thread pitch=about 2.5 mm; Thread Root @ 4 mm=27.4 mm.

In an embodiment of the disclosure, the closure is made using an injection molding process to prepare a PCO 1881 CSD closure, having a weight of about 2.15 grams and having the following dimensions: Closure height (not including Tamper Ring)=about 10.7 mm; Closure height with Tamper Ring=about 15.4 mm; Outside diameter @ 4 mm=about 29.6 mm; Thread diameter=about 25.5 mm; Bump seal diameter=about 24.5 mm; Bump seal thickness=about 0.7 mm; Bump seal height to center of olive=about 1.5 mm; Bore seal diameter=about 22.5 mm; Bore seal thickness=about 0.9 mm; Bore height to center of olive=about 1.6 mm; Top panel thickness=about 1.2 mm; Tamper band undercut diameter=about 26.3 mm; Thread depth=about 1.1 mm; Thread pitch=about 2.5 mm; Thread Root @ 4 mm=27.4 mm.

In an embodiment of the disclosure, the closure is made using a continuous compression molding process to prepare a PCO 1881 CSD closure, having a weight of about 2.15 grams and having the following dimensions: Closure height (not including Tamper Ring)=about 10.7 mm; Closure height with Tamper Ring=about 15.4 mm; Outside diameter @ 4 mm=about 29.6 mm; Thread diameter=about 25.5 mm; Bump seal diameter=about 24.5 mm; Bump seal thickness=about 0.7 mm; Bump seal height to center of olive=about 1.5 mm; Bore seal diameter=about 22.5 mm; Bore seal thickness=about 0.9 mm; Bore height to center of olive=about 1.6 mm; Top panel thickness=about 1.2 mm; Tamper band undercut diameter=about 26.3 mm; Thread depth=about 1.1 mm; Thread pitch=about 2.5 mm; Thread Root @ 4 mm=27.4 mm.

The disclosure is further illustrated by the following non-limiting examples.

EXAMPLES

General Polymer Characterization Methods

Melt indexes, I₂, I₅, I₆ and I₂₁ for the bimodal polyethylene composition were measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg, a 5 Kg, a 6.48 kg and a 21 kg weight respectively).

M_(n), M_(w), and M_(z) (g/mol) were determined by high temperature Gel Permeation Chromatography (GPC) with differential refractive index (DRI) detection using universal calibration (e.g. ASTM-D6474-99). GPC data was obtained using an instrument sold under the trade name “Waters 150c”, with 1,2,4-trichlorobenzene as the mobile phase at 140° C. The samples were prepared by dissolving the polymer in this solvent and were run without filtration. Molecular weights are expressed as polyethylene equivalents with a relative standard deviation of 2.9% for the number average molecular weight (“Mn”) and 5.0% for the weight average molecular weight (“Mw”). The molecular weight distribution (MWD) is the weight average molecular weight divided by the number average molecular weight, Mw/M_(n). The z-average molecular weight distribution is M_(z)/M_(n). Polymer sample solutions (1 to 2 mg/mL) were prepared by heating the polymer in 1,2,4-trichlorobenzene (TCB) and rotating on a wheel for 4 hours at 150° C. in an oven. The antioxidant 2,6-di-tert-butyl-4-methylphenol (BHT) was added to the mixture in order to stabilize the polymer against oxidative degradation. The BHT concentration was 250 ppm. Sample solutions were chromatographed at 140° C. on a PL 220 high-temperature chromatography unit equipped with four Shodex columns (HT803, HT804, HT805 and HT806) using TCB as the mobile phase with a flow rate of 1.0 mL/minute, with a differential refractive index (DRI) as the concentration detector. BHT was added to the mobile phase at a concentration of 250 ppm to protect the columns from oxidative degradation. The sample injection volume was 200 mL. The raw data were processed with Cirrus GPC software. The columns were calibrated with narrow distribution polystyrene standards. The polystyrene molecular weights were converted to polyethylene molecular weights using the Mark-Houwink equation, as described in the ASTM standard test method D6474.

Primary melting peak (° C.), heat of fusion (J/g) and crystallinity (%) was determined using differential scanning calorimetry (DSC) as follows: the instrument was first calibrated with indium; after the calibration, a polymer specimen is equilibrated at 0° C. and then the temperature was increased to 200° C. at a heating rate of 10° C./min; the melt was then kept isothermally at 200° C. for five minutes; the melt was then cooled to 0° C. at a cooling rate of 10° C./min and kept at 0° C. for five minutes; the specimen was then heated to 200° C. at a heating rate of 10° C./min. The DSC Tm, heat of fusion and crystallinity are reported from the 2^(nd) heating cycle.

The short chain branch frequency (SCB per 1000 carbon atoms) of the high density bimodal polyethylene composition was determined by Fourier Transform Infrared Spectroscopy (FTIR) as per the ASTM D6645-01 method. A Thermo-Nicolet 750 Magna-IR Spectrophotometer equipped with OMNIC version 7.2a software was used for the measurements. Unsaturations in the high density bimodal polyethylene composition were also determined by Fourier Transform Infrared Spectroscopy (FTIR) as per ASTM D3124-98. Comonomer content can also be measured using ¹³C NMR techniques as discussed in Randall, Rev. Macromol. Chem. Phys., C29 (2&3), p 285; U.S. Pat. No. 5,292,845 and WO 2005/121239.

Polyethylene composition density (g/cm³) was measured according to ASTM D792.

Hexane extractables were determined according to ASTM D5227.

Shear viscosity was measured by using a Kayeness WinKARS Capillary Rheometer (model # D5052M-115). For the shear viscosity at lower shear rates, a die having a die diameter of 0.06 inch and L/D ratio of 20 and an entrance angle of 180 degrees was used. For the shear viscosity at higher shear rates, a die having a die diameter of 0.012 inch and L/D ratio of 20 was used.

The Shear Viscosity Ratio as the term is used in the present disclosure is defined as: _(η10/η1000) at 240° C. The _(η10) is the melt shear viscosity at the shear rate of 10 s⁻¹ and the _(η1000) is the melt shear viscosity at the shear rate of 1000 s⁻¹ measured at 240° C.

The “Rosand” melt strength of the bimodal polyethylene composition was measured on Rosand RH-7 capillary rheometer (barrel diameter=15 mm) with a flat die of 2-mm Diameter, L/D ratio 10:1 at 190° C. Pressure Transducer: 10,000 psi (68.95 MPa). Piston Speed: 5.33 mm/min. Haul-off Angle: 52°. Haul-off incremental speed: 50-80 m/min² or 65±15 m/min². A polymer melt is extruded through a capillary die under a constant rate and then the polymer strand is drawn at an increasing haul-off speed until it ruptures. The maximum steady value of the force in the plateau region of a force versus time curve is defined as the melt strength for the polymer.

To determine CDBI₅₀, a solubility distribution curve is first generated for the polyethylene composition. This is accomplished using data acquired from the TREF technique. This solubility distribution curve is a plot of the weight fraction of the copolymer that is solubilized as a function of temperature. This is converted to a cumulative distribution curve of weight fraction versus comonomer content, from which the CDBI₅₀ is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 50% of the median comonomer content on each side of the median (See WO 93/03093 and U.S. Pat. No. 5,376,439). The CDBI₂₅ is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 25% of the median comonomer content on each side of the median.

The specific temperature rising elution fractionation (TREF) method used herein was as follows. Polymer samples (50 to 150 mg) were introduced into the reactor vessel of a crystallization-TREF unit (Polymer ChAR®). The reactor vessel was filled with 20 to 40 ml 1,2,4-trichlorobenzene (TCB), and heated to the desired dissolution temperature (e.g., 150° C.) for 1 to 3 hours. The solution (0.5 to 1.5 ml) was then loaded into the TREF column filled with stainless steel beads. After equilibration at a given stabilization temperature (e.g., 110° C.) for 30 to 45 minutes, the polymer solution was allowed to crystallize with a temperature drop from the stabilization temperature to 30° C. (0.1 or 0.2° C./minute). After equilibrating at 30° C. for 30 minutes, the crystallized sample was eluted with TCB (0.5 or 0.75 mL/minute) with a temperature ramp from 30° C. to the stabilization temperature (0.25 or 1.0° C./minute). The TREF column was cleaned at the end of the run for 30 minutes at the dissolution temperature. The data were processed using Polymer ChAR software, Excel spreadsheet and TREF software developed in-house.

The melt index, I₂ and density of the first and second ethylene copolymers were estimated by GPC and GPC-FTIR deconvolutions as discussed further below.

High temperature GPC equipped with an online FTIR detector (GPC-FTIR) was used to measure the comonomer content as the function of molecular weight. Mathematical deconvolutions are performed to determine the relative amount of polymer, molecular weight and comonomer content of the component made in each reactor, by assuming that each polymer component follows a Flory's molecular weight distribution function and it has a homogeneous comonomer distribution across the whole molecular weight range.

For these single site catalyzed resins, the GPC data from GPC chromatographs was fit based on Flory's molecular weight distribution function.

To improve the deconvolution accuracy and consistency, as a constraint, the melt index, I₂, of the targeted resin was set and the following relationship was satisfied during the deconvolution: Log₁₀(I ₂)=22.326528+0.003467*[Log₁₀(M _(n))]³−4.322582*Log₁₀(M _(w))−0.180061*[Log₁₀(M _(z))]²+0.026478*[Log₁₀(M _(z))]³ where the experimentally measured overall melt index, I₂, was used on the left side of the equation, while M_(n) of each component (M_(w)=2×M_(n) and M_(z)=1.5×M_(w) for each component) was adjusted to change the calculated overall M_(n), M_(w) and M_(z) of the composition until the fitting criteria were met. During the deconvolution, the overall M_(n), M_(w) and M_(z) are calculated with the following relationships: M_(n)=1/Sum(w_(i)/M_(n)(i)), M_(w)=Sum(w_(i)×M_(w)(i)), M_(z)=Sum(w_(i)×M_(z)(i)²), where i represents the i-th component and w_(i) represents the relative weight fraction of the i-th component in the composition.

The uniform comonomer distribution (which results from the use of a single site catalyst) of the resin components (i.e., the first and second ethylene copolymers) allowed the estimation of the short chain branching content (SCB) from the GPC-FTIR data, in branches per 1000 carbon atoms and calculation of comonomer content (in mol %) and density (in g/cm³) for the first and second ethylene copolymers, based on the deconvoluted relative amounts of first and second ethylene copolymer components in the polyethylene composition, and their estimated resin molecular weight parameters from the above procedure.

A component (or composition) density model and a component (or composition) melt index, I₂, model was used according to the following equations to calculate the density and melt index I₂ of the first and second ethylene polymers: density=0.979863−0.00594808*(FTIR SCB/1000 C)^(0.65)−0.000383133*[Log₁₀(M_(n))]³ 0.00000577986*(M_(w)/M_(n))₃+0.00557395*(M_(z)/M_(w))^(0.25); Log₁₀(melt index, I₂)=22.326528+0.003467*[Log₁₀(M_(n))]³ −4.322582*Log₁₀(M_(w))−0.180061*[Log₁₀(M_(z))]²+0.026478*[Log₁₀(M_(z))]³

where the M_(n), M_(w) and M_(z) were the deconvoluted values of the individual ethylene polymer components, as obtained from the results of the above GPC deconvolutions. Hence, these two models were used to estimate the melt indexes (I₂) and the densities of the components (i.e., the first and second ethylene copolymers).

Plaques molded from the polyethylene compositions were tested according to the following ASTM methods: Bent Strip Environmental Stress Crack Resistance (ESCR) at Condition B at 10% IGEPAL at 50° C., ASTM D1693; notched Izod impact properties, ASTM D256; Flexural Properties, ASTM D 790; Tensile properties, ASTM D 638; Vicat softening point, ASTM D 1525; Heat deflection temperature, ASTM D 648.

Dynamic mechanical analyses were carried out with a rheometer, namely Rheometrics Dynamic Spectrometer (RDS-II) or Rheometrics SR5 or ATS Stresstech, on compression molded samples under nitrogen atmosphere at 190° C., using 25 mm diameter cone and plate geometry. The oscillatory shear experiments were done within the linear viscoelastic range of strain (10% strain) at frequencies from 0.05 to 100 rad/s. The values of storage modulus (G′), loss modulus (G″), complex modulus (G*) and complex viscosity (η*) were obtained as a function of frequency. The same rheological data can also be obtained by using a 25 mm diameter parallel plate geometry at 190° C. under nitrogen atmosphere. The SHI_((1,100)) value is calculated according to the methods described in WO 2006/048253 and WO 2006/048254.

Closures

Generally, the mechanically sealing surfaces between a polyethylene closure and PET bottle neck finish have very complex geometries. As such, it is difficult to perform a systematic study using general experimental methods. For example, numerical simulations (e.g., Finite Element Analysis) may be useful for this purpose, but the inputs of the material properties for this type of analysis generally use those from compression-molded plaques made in a laboratory environment. Compression molded plaques however, may have very different material morphologies and properties than those of a closure manufactured with industrial injection molding or continuous compression molding processes. A methodology which can be used to obtain closure strain model parameters on closures that have been made according to commercial practices provides an alternative. One such methodology, also used in the present disclosure, was recently disclosed at an ANTEC™ meeting as “Deformation Measurement, Modeling and Morphology Study for HDPE Caps and Closures”, XiaoChuan (Alan) Wang, Mar. 23-25, 2015, Orlando, Fla., USA.

The methodology used in the present disclosure is to use the deformation (e.g., creep) of the top panel of an as-is closure to approximate that between the mechanically sealing surfaces of the plastic closure and PET bottle neck finish after a closure is put or screwed onto a PET bottle (see FIGS. 1-5 in “Deformation Measurement, Modeling and Morphology Study for HDPE Caps and Closures”, XiaoChuan (Alan) Wang, Mar. 23-25, 2015, Orlando, Fla., USA, ANTEC meeting). The use of a closure, instead of a standardized plaque, reflects the true molded material morphology and includes the contribution of the closure design. The deformation of the top panel of the closure can be well defined for the purpose of comparing closures made from different materials. By examining the top panel of the closure, one avoids dealing with the complex geometries of the sealing surfaces.

The following measurements and modeling can be used for any “as-is” closure design, provided that the closures being compared are prepared using substantially the same method under substantially similar conditions to provide closures having substantially similar design and dimensions. By way of non-limiting example only, the following method of preparing closures, closures which can then be compared using the methods described herein, is provided.

Method of Making a Closure by Injection Molding

A Sumitomo injection molding machine and 2.15-gram PCO (plastic closure only) 1881 carbonated soft drink (CSD) closure mold was used to prepare the closures herein. A Sumitomo injection molding machine (model SE75EV C250M) having a 28 mm screw diameter was used. The 4-cavity CSD closure mold was manufactured by Z-moulds (Austria). The 2.15-gram PCO 1881 CSD closure design was developed by Universal Closures Ltd. (United Kingdom). During the closure manufacturing, four closure parameters, the diameter of the top of the cap, the bore seal diameter, the tamper band diameter and the overall cap height, were measured and ensured to be within quality-control specifications.

For red pigmented closures, resins are dry-blended with 2% slip (erucamide) master batch (Ampacet slip 101797 with the 5 wt % slip; 1000 ppm slip additive in the final resin) and 1% of red masterbatch (Ampacet PE red masterbatch LJ-206971 with 1.5 wt. % red pigment; 150 ppm red pigment in the final resin) prior to injection molding.

An International Society of Beverage Technologists (ISBT) voluntary standard test method was used to determine the closure dimensions. The test used involves the selection of a mold cavity and the measurements on at least 5 closures made from that particular cavity. At least 14 dimensional measurements were obtained from closures that were aged for at least 1 week from the date of production. The closure dimension measurements was performed using a Vision Engineering, Swift Duo dual optical and video measuring system. All measurements were taken using 10× magnification and utilizing Metlogix M video measuring system software (see MetLogix M³: Digital Comparator Field of View Software, User's Guide).

Example 1 (Comparative) is a closure made from a unimodal polyethylene resin having a melt index I₂ of 32 g/10 min, a density of 0.951 g/cm³, and a weight average molecular weight Mw/Mn of 2.88, and which is made using a Ziegler-Natta catalyst in a solution olefin polymerization process. This resin is commercially available from NOVA Chemicals Corporation as SCLAIR® 2712. A GPC profile for the resin is given in FIG. 1A.

Example 2 is a closure made from a bimodal polyethylene composition and has a melt index I₂ of 1.5 g/10 min, a density of 0.953 g/cm³, and a weight average molecular weight Mw/Mn of 8.47. The bimodal polyethylene composition used in Example 2, was made using a single site catalyst in a solution olefin polymerization process. Further details on the bimodal polyethylene composition used in Example 2 and methods of its preparation are disclosed in U.S. Pat. No. 8,962,755, which is incorporated herein by reference in its entirety. A GPC profile for the resin is given in FIG. 1B.

The polymers used to make closures in Examples 1 and 2 are shown in Table 1A, along with their plaque data. The data for the first and second ethylene co polymer components of Example 2 are shown in Table 1B. The closures were formed by injection molding, and the injection-molding processing conditions are given in Table 2. Closure dimensions are provided in Table 3.

TABLE 1A Polymer Properties and Plaque Data Example 1, Comp. 2 Polymer Modality Unimodal Bimodal Alpha Olefin Comonomer 1-butene 1-octene I₂, g/10 min 32 1.42 Density, g/cm³ 0.951 0.9533 I₂₁/I₂ 22.7 58 Stress Exponent 1.24 1.35 Mn (g/mol) 14928 11687 Mw (g/mol) 43003 95252 Mz (g/mol) 95318 303871 Mw/Mn 2.88 8.15 CDBI₅₀ (%) 68.7 71.6 CDBI₂₅ (%) 50.5 63.3 DSC Primary Melting Peak (° C.) 126.99 128.92 Heat of Fusion (J/g) 210.4 231.6 Crystallinity (%) 72.55 83.6 FTIR Short chain branching per 1000 carbons 1.3 2.6 (uncorrected for chain end —CH₃) Internal unsaturation (No. per 100 carbons) 0.008 0.002 Side chain unsaturation (No. per 100 carbons) 0.005 0 Terminal unsaturation (No. per 100 carbons) 0.085 0.008 Plaque 2% secant flexural modulus (MPa) 786 1119 ESCR Cond. B at 10% (hrs) 0 145 Heat Deflection Temperature at 66 psi (° C.) 66 66.7 VICAT Softening Point (° C.) 122 126.2 Notched Izod Impact Strength (ft-lb/in) 0.66 1.4 Hexane extractables (wt. %) 0.43 0.34

TABLE 1B Example 2, Component Properties First Ethylene Copolymer Weight fraction 0.44 Mw 178000 I₂ (g/10 min) 0.10 Density, d1 (g/cm³) 0.9326 Comonomer Octene SCB1/1000C 1.27 SCB1 mol % 0.25 Second Ethylene Copolymer Weight fraction 0.56 Mw 12900 I₂ (g/10 min) 3353 Density, d2 (g/cm³) 0.9612 Comonomer Octene SCB2/1000C 0.47 SCB2 mol % 0.09 Estimated (d2 − d1), g/cm³ 0.0286 Estimated SCB1/SCB2 2.70

TABLE 2 Injection Molding Processing Conditions Example 1, Comp. 2 Additives (Color & Formulation) 1% red, 2% slip 1% red, 2% slip (1000 ppm slip) (1000 ppm slip) Part Weight - 4 cavities (g) 8.653 8.613 Cycle time (s) 3.631 3.874 Injection Speed (mm/s) 45 45 Filling time (s) 0.661 0.679 Dosing time (s) 1.788 2.152 Minimum Cushion (mm) 9.758 9.765 Filling peak pressure (psi) 8294.6 15271.2 Full peak pressure (psi) 8345 15272.9 Hold end position (mm) 12.144 12.43 Clamp force (ton) 17.1 19.2 Fill start position (mm) 39.461 40.41 Dosing back pressure (psi) 824.2 809.9 Pack pressure (psi) 8286.7 12516.1 Filling time 1 (s) 0.665 0.682 Temperature zone 1 (° C.) 180 180 Temperature zone 2 (° C.) 185 185 Temperature zone 3 (° C.) 190 190 Temperature zone 4 (° C.) 200 200 Temperature zone 5 (° C.) 200 200 Mold temperature stationary (° F.) 58 58 Mold temperature moving (° F.) 58 58

TABLE 3 Closure Dimensions Example 1, Comp. 2 Additives (Color & Formulation) 1% red, 2% slip 1% red, 2% slip (1000 ppm slip) (1000 ppm slip) Closure height no Tamper Ring 10.67 10.67 (mm) Closure height with Tamper Ring 15.44 15.34 (mm) Outside diameter @ 4 mm 29.58 29.53 (mm) Thread diameter (mm) 25.54 25.55 Bump seal diameter (mm) 24.52 24.45 Bump seal thickness (mm) 0.68 0.71 Bump seal height to center of 1.52 1.55 olive (mm) Bore seal diameter (mm) 22.5 22.38 Bore seal thickness (mm) 0.91 0.92 Bore height to center of olive 1.58 1.70 (mm) Top panel thickness (mm) 1.21 1.21 Tamper band undercut diameter 26.29 26.15 (mm) Thread depth (mm) 1.06 1.04 Thread pitch (mm) 2.54 2.67 Thread Root @ 4 mm (mm) 27.35 27.32 Cap weight (g) 2.164 2.157 Deformation Analysis of Solid-State Closures

A DHR-3 rotational rheometer testing bar was modified by attaching an annular probe (see FIGS. 2A and 2B) to its end. This set up was used for the compressive deformation tests. The rheometer has a temperature chamber (oven) that allows one to measure the deformation responses at different temperatures. The annular probe made had an inner diameter of 6.4 mm and an outer diameter of 10.8 mm. The annular structure is designed to avoid contact of the probe with the center of the top panel of a closure since sometimes the gate mark (due to the nature of the injection molding process) is not completely flat (note: closures made by continuous compression molding processes will normally not have such marks at the center of the top panel of the closure). A closure holder (see FIG. 3) was also designed to hold the closure. This holder has four setting screws to fix the position of the closure inside the holder. The probe is glued to the testing bar using high temperature resistant silicone grease. The projected or contact area of the closure surface to be put under stress was 0.5944 cm². Tamper-evident rings were removed from the closures prior to testing, so that only the deformation of the top panel at the projected area was induced. The closure without tamper-evident ring is fixed in the stainless steel secure ring closure holder (see FIG. 3) and placed on the bottom plate of the rheometer. The point where the probe first touches the closure is set as the zero position. For the time sweep test, the sample was conditioned in the oven for 15 minutes at 93° C. before the testing started. A person skilled in the art will recognize that the present testing can be carried out at any suitable temperature for obtaining results, and especially any temperature above ambient to obtain results applicable to use of closures in hot fill or aseptic fill processes. An initial 2.5 N compression force was applied and then the time sweep was carried out with 1 rad/s frequency and 0.0001% radial strain for 300 seconds at 93° C. (which at such a low value does not affect axial responses; if higher radial strain were used, the solid samples might induce distortions in the axial force and deformation, ΔL data obtained). During this process, the instantaneous compressive force and deformation measured as ΔL vs. time were recorded. The compressive strain ε (taken as a positive value for modeling purposes, see below) is calculated by taking the ratio of ΔL/thickness (in mm) of the closure top panel. The stress undergone at the contact area is calculated by using the recorded force divided by the actual contact area (i.e., 0.5944 cm²). The data provided in Table 4 is an example data set obtained for each closure, and came from the modified solid-state deformation analysis carried out on each closure (Time in seconds, Axial Force in Newtons, Deformation or DL in mm, Temperature in ° C. and Angular Frequency, in radians per second). The data from each closure was modeled to obtain the strain model parameters (A, n and m). The data reported in Tables 4A and 4B show one set of values for the raw data obtained by the above described deformation test for each closure made of a specific resin. In practice, data were collected for 4 to 6 closures made from each resin. The data from the 4-6 closures measured for each resin type was used as the basis for modeling after converting the axial force to stress and the deformation to strain. The numbers obtained with the model (on the closure/resin systems) were then averaged and are provided below in Table 5. Without wishing to be bound by theory, it is believed that the compressive deformation resistance evaluated using the current methodology also reflects the deformation resistance under any other deformation modes, such as tensile deformation; it is further believed that the deformation of the top panel of an as-is closure approximates that which occurs between the mechanically sealing surfaces of a plastic closure and a PET bottle neck finish after a closure is secured to a PET bottle.

TABLE 4A Example 1 Top panel Angular thickness Projected Temperature frequency Stress Time (s) Force (N) DL (mm) (mm) Area (cm²) (° C.) (rad/s) Strain (N/cm²) 13.1815 0.3748 0.1319 1.21 0.5944 93.01 1 10.9% 0.6305 27.1430 0.9321 0.1827 1.21 0.5944 93 1 15.1% 1.5681 41.2604 1.3460 0.2207 1.21 0.5944 93 1 18.2% 2.2644 55.0815 1.6385 0.2480 1.21 0.5944 93.01 1 20.5% 2.7566 68.9493 1.8469 0.2687 1.21 0.5944 93.01 1 22.2% 3.1071 83.5972 2.0062 0.2853 1.21 0.5944 93.01 1 23.6% 3.3751 97.5586 2.1170 0.2974 1.21 0.5944 93 1 24.6% 3.5616 111.3953 2.1974 0.3067 1.21 0.5944 92.99 1 25.3% 3.6969 125.3256 2.2625 0.3141 1.21 0.5944 93 1 26.0% 3.8064 139.3807 2.3090 0.3201 1.21 0.5944 93 1 26.5% 3.8846 153.4513 2.3473 0.3249 1.21 0.5944 93 1 26.9% 3.9490 167.3348 2.3736 0.3288 1.21 0.5944 92.99 1 27.2% 3.9933 181.2494 2.3928 0.3319 1.21 0.5944 93 1 27.4% 4.0256 195.1485 2.4085 0.3347 1.21 0.5944 92.99 1 27.7% 4.0520 208.9384 2.4204 0.3370 1.21 0.5944 93 1 27.9% 4.0720 222.9310 2.4293 0.3391 1.21 0.5944 93 1 28.0% 4.0869 237.0173 2.4381 0.3409 1.21 0.5944 92.99 1 28.2% 4.1018 251.0100 2.4449 0.3425 1.21 0.5944 93 1 28.3% 4.1132 264.7530 2.4306 0.3425 1.21 0.5944 92.99 1 28.3% 4.0891 278.3245 2.4216 0.3425 1.21 0.5944 93 1 28.3% 4.0740 292.0208 2.4114 0.3425 1.21 0.5944 93 1 28.3% 4.0569 305.8886 2.4020 0.3425 1.21 0.5944 92.99 1 28.3% 4.0411

TABLE 4B Example 2 Top panel Angular thickness Projected Temperature frequency Stress Time (s) Force (N) DL (mm) (mm) Area (cm²) (° C.) (rad/s) Strain (N/cm²) 13.36869 0.4928 0.1324 1.21 0.5944 93.01 1 10.9% 0.829066 27.43934 1.30707 0.1753 1.21 0.5944 93.01 1 14.5% 2.198974 41.43201 1.7573 0.2014 1.21 0.5944 93.03 1 16.6% 2.956427 55.25308 2.01503 0.2178 1.21 0.5944 93 1 18.0% 3.390023 69.23014 2.16714 0.2289 1.21 0.5944 93 1 18.9% 3.645929 83.09801 2.27232 0.2365 1.21 0.5944 93.01 1 19.5% 3.82288 97.13747 2.33466 0.2419 1.21 0.5944 93.01 1 20.0% 3.927759 111.1769 2.37277 0.246 1.21 0.5944 93 1 20.3% 3.991874 125.0604 2.39967 0.2491 1.21 0.5944 93 1 20.6% 4.03713 139.0687 2.42115 0.2516 1.21 0.5944 93 1 20.8% 4.073267 153.0457 2.43668 0.2535 1.21 0.5944 93 1 21.0% 4.099395 167.054 2.44276 0.2552 1.21 0.5944 93 1 21.1% 4.109623 181.0934 2.42515 0.2554 1.21 0.5944 92.99 1 21.1% 4.079996 194.8937 2.40547 0.2555 1.21 0.5944 92.99 1 21.1% 4.046887 208.4644 2.4357 0.2574 1.21 0.5944 93 1 21.3% 4.097745 222.1139 2.41572 0.2574 1.21 0.5944 93 1 21.3% 4.064132 235.8881 2.40464 0.2574 1.21 0.5944 92.99 1 21.3% 4.045491 249.3972 2.4316 0.2591 1.21 0.5944 92.99 1 21.4% 4.090848 263.1871 2.41641 0.2591 1.21 0.5944 92.99 1 21.4% 4.065293 276.7274 2.40486 0.2591 1.21 0.5944 93 1 21.4% 4.045861 290.5016 2.42899 0.2606 1.21 0.5944 93 1 21.5% 4.086457 304.0263 2.41687 0.2607 1.21 0.5944 92.99 1 21.5% 4.066067

A person skilled in the art will recognize that any resin which is capable of being formed into a closure may be subjected to similar testing to provide inputs for use in the compressive strain model, so that two or more closures made of different polymeric material may be directly compared and contrasted with respect to their respective deformation behavior.

The Compressive Strain Model

Without wishing to be bound by any single theory, the responses collected for each closure reflect the characteristics of the resin used in each closure. However, since the instantaneous compressive deformation information is a function of both time and stress, which is a non-linear relationship or typical multivariate phenomenon, a model is employed to provide a better understanding of the polymer structure-closure property relationship. The model used here is a model that can adequately describe the closure deformation as a function of stress and time at a given temperature for each polymer-closure pairing.

The compressive strain data obtained as described above are modeled using a compressive strain model in order to compare the tendency of a polymer-closure system to deform under stress. Together with the compressive strain data, the model is a useful method to provide rapid and cost effective manner by which to predict polymer-closure pairing deformation properties.

The compressive strain is assumed to follow the mathematical form at a given temperature as shown below: ε=Δ×σ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent. Any software capable of performing non-linear regressions can be used to estimate the model parameters.

FIG. 4 shows the actual and fitted compressive strains (deformations) using the compressive strain model for Examples 1 and 2. Generally, the model fits very well with the actual deformation obtained from the closures made from the different polymer types. The average values of the fitted model parameters, A, n and m, are summarized in Table 5.

TABLE 5 Compressive Strain Model Parameters for Closures Made of Different Polyethylene Polymers Example 1, Comp. 2 Additives (Color & Slip 1% red, 2% slip MB 1% red, 2% slip MB by Masterbatch, MB) (1000 ppm slip) (1000 ppm slip) Model Coefficient, A 0.093679 1% red, 2% slip MB (1000 ppm slip) Deformation stress 0.348888 0.092886 exponent, n Time Exponent, m 0.115313 0.335115 Predicted creep strain 29.4% 0.078648 at 93° C., 4N/cm², 305 seconds; the stress is constant and creep is the deformation vs time

Predicted creep strain (also shown in Table 5) is the deformation of a material at a specific time under a constant stress. Since the model described above for compressive strain fits the actual raw data very well, the model may be further used to predict the deformations under different conditions, such as increased stress levels, or predicting compressive strain at various stress values at a constant loading time.

The data provided in Table 5 clearly shows that Example 2 has a lower time exponent (m) value and better creep or deformation resistance when compared to Example 1. The time exponent value for Example 2 is lower than 0.105. The lower the time exponent value with A and n parameters being essentially the same, the better the closure/polymer system resists deformation. As the deformation at elevated temperature is believed to be important to whether a particular polymer/closure system is suitable for a use in a hot-filling or aseptic filling process, the present model helps to establish which polyethylene resins are suitable in such end use applications.

Preparation of a Liquid Containing 4.2 Volume % CO₂ Sealed in a PET Container with a Closure

To prepare 4.2 vol % of carbon dioxide, CO₂ (4.2 Gas Volume or “GV”) in purified water, 10.13 grams of sodium bicarbonate (NaHCO₃) and 7.72 grams of citric acid (C₆H₈O₇) were packed into two water-soluble EVOH (ethylene vinyl alcohol) bags. Next, 600 mL of purified water was added to a PET bottle filling the bottle. Each bottle had a PCO 1881 neck finish. The bag with sodium bicarbonate and the bag with citric acid were then added to the PET bottle filled with purified water. A closure was immediately placed on the PET bottle with manual force and turned at an application angle 360°. Next the bottle-closure system was placed in a Steinfurth torque measuring machine with a proper chuck to further turn the closure at an application angle of 380° at a speed of 0.8 rpm/minute. The bottle was then shaken to ensure complete dissolution of the chemicals in water.

Elevated Temperature Cycle Test (ETCT)

This is an International Society of Beverage Technologists (ISBT) voluntary standard test. As closures may experience wide temperature swings in hot weather markets, it is essential that the closure remain on the neck finish during these temperature swings and throughout the shelf life of the product. The elevated temperature cycle test evaluates such closure performance.

After filling and capping a PET bottle with 4.2 GV of CO₂ as described above, the PET bottle-closure system was placed in a temperature controlled chamber. The bottle-closure system was then exposed to the following temperature program: Cycle 1; A) hold at 60° C. for 6 hours, then B) at 32° C. for 18 hours; Cycle 2; C) hold at 60° C. for six 6 hours, then D) at 32° C. for 18 hours; Cycle 3; E) hold at 60° C. for 6 hours, then F) at 32° C. for 18 hours. After each cycle component, the PET bottle-closure samples were observed for closure releases, cocked and deformed closures and leakers. A total of 24 bottle-closure systems were tested in each example. The results are shown in Table 6.

TABLE 6^(1,2) Elevated Temperature Cycle Test of a PET Bottle - PE Closure System (closure has additives for color, 1% red, and slip, 1000 ppm by way of 2% masterbatch) Cycle No. of Visual Inspection % Pass Example Cycle Half Failures Notes (no issue) 1, Comp. 1 A No failure 33.3% B No failure 2 C 2 Nos. 10 and 24 had visual flaws D 4 Nos. 4, 6, 7, and 21 had visual flaws 3 E 3 Nos. 12 and 20 had visual flaws; No. 11 vented gas F 7 Nos. 2 and 3 had visual flaws; Nos. 5, 14, 17, 22, and 23 vented gas 2 1 A 0 No failures  100% 1 B 0 No failures 2 C 0 No failures 2 D 0 No failures 3 E 0 No failures 3 F 0 No failures Notes: ¹PET bottle used: PCO 1881 neck finish, 591 ml. ²No. of specimens: 24

Examination of the data in Table 6, shows that Example 1, where the closure is made from a unimodal polyethylene composition (SCLAIR 2712) has inferior heat cycling performance when compared to Example 2, where the closure is made from a bimodal polyethylene composition. For Example 2, no failures in the closure were observed under any of the temperature cycle conditions imposed, while for Example 1, the closure failed in numerous cases when temperature cycles 2 and 3 were reached. Example 2 closures had a 100% pass rate, while Example 1 closures had a 33% pass rate.

Secure Seal Test (SST)

As PET (or glass) is more rigid than polyethylene, the deformation at the mechanically sealing surfaces of a bottle and closure package likely occurs more with the plastic closure than the bottle. Hence, it is important that the plastic closure has an appropriate deformation. Without wishing to be bound by theory, it is expected that an excessive deformation of the closure at the mechanically sealing surfaces may lead to the loss of the intimate engagement of the sealing surfaces at some point. Insufficient deformation of the closure at the mechanically sealing surfaces may not provide sufficient conformability to the shapes of the sealing surfaces on the rigid PET bottle neck finish. Appropriate deformation at the mechanically sealing surfaces can provide the intimate engagement between the sealing surfaces of the bottle (neck finish) and closure. Hence, a closure exhibiting excessive compressive strain or excessive deformation may lead to poorer sealing properties (e.g., decreased tightness) when the closure is fitted to a PET container, bottle and the like; alternatively, a closure exhibiting appropriate compressive strain or deformation may lead to improved sealing properties (e.g., improved tightness) when the closure is fitted to a PET container, bottle and the like.

The SST is an International Society of Beverage Technologists (ISBT) voluntary standard test. This test is to determine the plastic closure seal and thread integrity while under an internal pressure. A detailed description of the test follows. After filling and capping a PET bottle with 4.2 GV of CO₂ as described above, the PET bottle-closure system was conditioned at room temperature (22° C.+/−1° C.) for 24 hours. Next, the PET bottle neck finish including the closure, was cut out using a Secure-Pak™ neck finish cutting tool. The combined neck finish/closure system was attached in a sealed fit with a pressure tubing and gas pressure was introduced. The PET neck finish/closure system was placed into a testing fixture and the entire assembly was placed into a water tank of a Secure Seal Tester, model SST, manufactured by Secure Pak (Maumee, Ohio). The test was carried out in water at room temperature (22° C.). The pressure was slowly applied to the interior of the closure to 100 psi and held for a period of 1 minute. The PET bottle neck finish-closure sample was observed for signs of air bubbles. A failure is indicated when a steady stream of bubbles emitting from the closure can be observed. In a next step, the pressure was increased to 175 psi and held for one 1 minute to again look for evidence of air bubbles. In a final step, the pressure was increased to 200 psi and held for 1 minute, and evidence of air bubbles was looked for. The pressures at which observable air leakage events occurred were recorded as well as the percentage of air passage.

A total of twenty Secure Seal Tests were carried out for each of Examples 1-2 and the results are provided in Table 7.

TABLE 7 Secure Seal Test (SST) of a PET Bottle - PE Closure System (closure has additives for color, 1% red, and slip, 1000 ppm by way of 2% masterbatch) Maximum Pressure attained Maximum P1 Leakage @ in psi with elapsed P1 Leakage @ Pressure attained in psi Specimen 100 psi, No. of time before failure Specimen 100 psi, No. of with elapsed time before Example No. failures (seconds) No. failures failure (seconds) 1, Comp. 1 0 175 (10 sec) 11 0 175 (12 sec) 2 0 155 12 0 200 3 0 175 (55 sec) 13 0 175 (37 sec) 4 0 135 14 0 175 (10 sec) 5 0 175 (45 sec) 15 0 175 (8 sec)  6 0 175 (0 sec)  16 0 175 (4 sec)  7 0 180 17 0 165 8 0 160 18 0 150 9 0 175 (8 sec)  19 0 160 10 0 175 (42 sec) 20 0 175 (9 sec)  No. of specimens not lasting 175 psi for 1 minute = 18; % Pass >175 psi for 1 minute = 10% 2 1 0 200 11 0 200 2 0 200 12 0 200 3 0 200 13 0 200 4 0 200 14 0 200 5 0 200 15 0 200 6 0 200 16 0 200 7 0 200 17 0 200 8 0 200 18 0 200 9 0 200 19 0 200 10 0 200 20 0 200 No. of specimens not lasting 175 psi for 1 minute = 0; % Pass >175 psi for 1 minute = 100%

Examination of the data in Table 7, shows that Example 1, where the closure is made from a unimodal polyethylene composition (SCALIR 2712) has inferior sealing properties when compared to Example 2, where the closure is made from a bimodal polyethylene composition. For Example 2, no failures were observed at pressures of up to 200 psi. For Example 1, only 10% of the closures passed the secure seal test at a pressure of more than 175 psi for more than 1 minute, while several began to fail at a pressure of below 175 psi.

Removal Torque Test

This is an International Society of Beverage Technologists (ISBT) voluntary standard test. It is used to determine the torque required to remove a closure from a container.

After filling and capping a PET bottle with 4.2 GV of CO₂ as described above, the bottle was conditioned for 24 hours at room temperature (22° C.+/−1° C.) prior to conducting the removal torque test. The total application angle used for testing was 740°. The maximum removal torque was tested using a Steinfurth automated torque measuring machine with a proper chuck at the speed of 0.8 rpm/minute. A total of twelve tests were carried out for each of Examples 1 and 2 and the average results are provided in Table 8.

TABLE 8¹ Removal Torque of a PET Bottle - PE Closure System (closure has additives for color, 1% red, and slip, 1000 ppm by way of 2% masterbatch) Average Std. Dev. Minimum Maximum Example (in-lb) (in-lb) (in-lb) (in-lb) 1, Comp. 12.6 0.88 11.7 14.4 2 15.4 1.23 13.4 17.6 Note ¹PET bottle used: CSD, PCO 1881 neck finish, 591 ml.

The data in Table 8, support the notion that the bimodal polyethylene composition in Example 2 leads to superior closure performance than the unimodal polyethylene composition. For the former, the average removal torque is 15.4 inches pound compared to 12.6 inches pound for the latter. Also, the minimum toque to remove the closure made with the bimodal resin in Example 2 is higher than that required for the closure made with SCLAIR 2712 (i.e., Example 1) which is indicative of improved sealing properties.

Ball Impact Test

This is an International Society of Beverage Technologists (ISBT) voluntary standard test. During transportation and use by the consumer, a beverage closure can experience impact forces. The ball impact test evaluates the tendency of the closure to remain on a container opening without release. The test was carried out as follows. After filling and capping a PET bottle-closure system with 4.2 GV of CO₂ as described above, the bottle-closure system was conditioned for 24 hours in a temperature controlled chamber at 4° C. Ball impact testing was conducted using Steinfurth Ball impact tester which holds the bottle-closure system against movement with the bottle-closure system held in a desired orientation. A steel ball (286.7 g, 41.27 mm in diameter) was used as the impacting object. The steel ball was dropped from a height of 762 mm (30 inches) at four different orientations; at 0° to the top center of the closure, at 90° to the top edge of the closure, at 45° to top edge of the closure, and at 90° to the sidewall edge of the closure. After the impact test, the bottle-closure system was removed from the impact tester and the closure was checked for damage and/or leakage. A total of ten ball impact tests were carried out at each angle for each of Examples 1 and 2 and the results are provided in Table 9.

TABLE 9¹ Ball Impact Test of PET Bottle - PE Closure System (closure has additives for color, 1% red, and slip, 1000 ppm by way of 2% masterbatch) Example 1, Comp. 2 0° to top center of closure 0 (100%) 0 (100%) No. of failures (% of pass) 90° to top edge of closure 7 (30%) 5 (50%) No. of failures (% of pass) 45° angle to top edge of closure 1 (90%) 2 (80%) No. of failures (% of pass) 90° to sidewall edge of closure 4 (60%) 0 (100%) No. of failures (% of pass) Total No. of failure 12 (70%) 7 (82.5%) (% of pass) Note ¹PET bottle used: CSD, PCO 1881 neck finish, 591 ml.

The data in Table 9 show that there is little difference between Examples 1 and 2 when the ball impact test is carried out at 0° to the top center of the closure. The closure of Example 2, comprising a bimodal high density polyethylene does however perform better when the test is carried out at 90° to the sidewall edge of the closure and 90° to the top edge of the closure. Also, the total number of failures is better when the bimodal polyethylene composition is used relative to the unimodal polyethylene composition (i.e., SCLAIR 2712).

Non-limited embodiments of the present disclosure include the following:

Embodiment A

A process to fill a container, the process comprising: adding a hot liquid to the container through a container opening, sealing the container opening with a closure comprising a bimodal polyethylene composition, and bringing the hot liquid into contact with an interior surface of the closure; wherein the bimodal polyethylene composition comprises:

(1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and

(2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0; a density of at least 0.949 g/cm³, a melt index I₂, of from 0.2 to 3.0 g/10 min; an M_(z) of less than 500,000; a stress exponent of less than 1.53, and an ESCR Condition B (10% IGEPAL) of at least 20 hrs.

Embodiment B

The process of Embodiment A wherein the first ethylene copolymer and the second ethylene copolymer are made using a single site catalyst.

Embodiment C

The process of Embodiment A or B wherein the first ethylene copolymer has a density of from 0.925 to 0.950 g/cm³.

Embodiment D

The process of Embodiment A, B or C wherein the second ethylene copolymer has a density of less than 0.965 g/cm³.

Embodiment E

The process of Embodiment A, B, C or D wherein the bimodal polyethylene composition has a density of from 0.951 to 0.960 g/cm³.

Embodiment F

The process of Embodiment A, B, C, D or E wherein the density of the second ethylene copolymer is less than 0.035 g/cm³ higher than the density of the first ethylene copolymer.

Embodiment G

The process of Embodiment A, B, C, D, E or F wherein the first and second ethylene copolymers have a M_(w)/M_(n) of less than 2.3.

Embodiment H

The process of Embodiment A, B, C, D, E, F or G wherein the bimodal polyethylene composition has a composition distribution breadth index (CDBI₂₅) of greater than 55% by weight.

Embodiment I

The process of Embodiment A, B, C, D, E, F, G or H wherein the bimodal polyethylene composition has a composition distribution breadth index (CDBI₅₀) of greater than 65% by weight.

Embodiment J

The process of Embodiment A, B, C, D, E, F, G, H or I wherein the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.5.

Embodiment K

The process of Embodiment A, B, C, D, E, F, G, H, I or J wherein the bimodal polyethylene composition comprises: from 30 to 60 weight percent of the first ethylene copolymer; and from 70 to 40 weight percent of the second ethylene copolymer.

Embodiment L

The process of Embodiment A, B, C, D, E, F, G, H, I, J, or K wherein the bimodal polyethylene composition further comprises a nucleating agent.

Embodiment M

The process of Embodiment A, B, C, D, E, F, G, H, I, J, K or L wherein the first and second ethylene copolymers are copolymers of ethylene and 1-octene.

Embodiment N

The process of Embodiment A, B, C, D, E, F, G, H, I, J, K, L or M wherein the closure is made by continuous compression molding or injection molding.

Embodiment O

The process of Embodiment A, B, C, D, E, F, G, H, I, J, K, L, M or N wherein the bimodal polyethylene composition is prepared by contacting ethylene and an alpha-olefin with a polymerization catalyst under solution polymerization conditions in a least two polymerization reactors.

Embodiment AA

Use of a closure in a hot fill process, wherein the closure comprises a bimodal polyethylene composition comprising:

(1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and

(2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0; a density of at least 0.949 g/cm³, a melt index I₂, of from 0.2 to 3.0 g/10 min; an M_(z) of less than 500,000; a stress exponent of less than 1.53, and an ESCR Condition B (10% IGEPAL) of at least 20 hrs.

Embodiment BB

The use of a closure according to Embodiment AA wherein the first ethylene copolymer and the second ethylene copolymer are made using a single site catalyst.

Embodiment CC

The use of a closure according to Embodiment AA or BB wherein the first ethylene copolymer has a density of from 0.925 to 0.950 g/cm³.

Embodiment DD

The use of a closure according to Embodiment AA, BB or CC wherein the second ethylene copolymer has a density of less than 0.965 g/cm³.

Embodiment EE

The use of a closure according to Embodiment AA, BB, CC or DD wherein the bimodal polyethylene composition has a density of from 0.951 to 0.957 g/cm³.

Embodiment FF

The use of a closure according to Embodiment AA, BB, CC, DD or EE wherein the density of the second ethylene copolymer is less than 0.035 g/cm³ higher than the density of the first ethylene copolymer.

Embodiment GG

The use of a closure according to Embodiment AA, BB, CC, DD, EE or FF wherein the first and second ethylene copolymers have a M_(w)/M_(n) of less than 2.3.

Embodiment HH

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF or GG wherein the bimodal polyethylene composition has a composition distribution breadth index (CDBI₂₅) of greater than 55% by weight.

Embodiment II

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG or HH wherein the bimodal polyethylene composition has a composition distribution breadth index (CDBI₅₀) of greater than 65% by weight.

Embodiment JJ

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG, HH or II wherein the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.5.

Embodiment KK

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG, HH, II or JJ wherein the bimodal polyethylene composition comprises: from 30 to 60 weight percent of the first ethylene copolymer; and from 70 to 40 weight percent of the second ethylene copolymer.

Embodiment LL

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG, HH, II, JJ or KK wherein the bimodal polyethylene composition further comprises a nucleating agent.

Embodiment MM

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG, HH, II, JJ, KK or LL wherein the first and second ethylene copolymers are copolymers of ethylene and 1-octene.

Embodiment NN

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG, HH, II, JJ, KK, LL or MM wherein the closure is made by continuous compression molding or injection molding.

Embodiment OO

The use of a closure according to Embodiment AA, BB, CC, DD, EE, FF, GG, HH, II, JJ, KK, LL, MM or NN wherein the bimodal polyethylene composition is prepared by contacting ethylene and an alpha-olefin with a polymerization catalyst under solution polymerization conditions in a least two polymerization reactors.

Embodiment AAA

A process to fill a container, the process comprising: adding a hot liquid to the container through a container opening; sealing the container opening with a closure comprising a bimodal polyethylene composition having a density of from 0.949 g/cm³ to 0.960 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min; and bringing the hot liquid into contact with an interior surface of the closure; wherein the closure has a time exponent, m of 0.105 or less where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

Embodiment BBB

The process of Embodiment AAA, wherein the bimodal polyethylene composition comprises:

(1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and

(2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5.

Embodiment AAAA

Use of a closure in a hot fill process, wherein the closure comprises a bimodal polyethylene composition having a density of from 0.949 g/cm³ to 0.960 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min; wherein the closure has a time exponent, m of 0.105 or less, where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.

Embodiment BBBB

The use of a closure in a hot fill process according to Embodiment AAAA, wherein the bimodal polyethylene composition comprises:

(1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and

(2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5.

The embodiments of the invention in which an exclusive property or privilege is claimed are defined as follows. 

What is claimed is:
 1. A process to fill a container, the process comprising: adding a hot liquid to the container through a container opening, sealing the container opening with a closure comprising a bimodal polyethylene composition, and bringing the hot liquid into contact with an interior surface of the closure; wherein the bimodal polyethylene composition comprises: (1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and (2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5; and wherein the bimodal polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0; a density of at least 0.949 g/cm³, a melt index I₂, of from 0.2 to 3.0 g/10 min; an M_(z) of less than 500,000; a stress exponent of less than 1.53, and an ESCR Condition B (10% IGEPAL) of at least 20 hrs.
 2. The process of claim 1 wherein the first ethylene copolymer and the second ethylene copolymer are made using a single site catalyst.
 3. The process of claim 1 wherein the first ethylene copolymer has a density of from 0.925 to 0.950 g/cm³.
 4. The process of claim 1 wherein the second ethylene copolymer has a density of less than 0.965 g/cm³.
 5. The process of claim 1 wherein the bimodal polyethylene composition has a density of from 0.951 to 0.960 g/cm³.
 6. The process of claim 1 wherein the density of the second ethylene copolymer is less than 0.035 g/cm³ higher than the density of the first ethylene copolymer.
 7. The process of claim 1 wherein the first and second ethylene copolymers have a M_(w)/M_(n) of less than 2.3.
 8. The process of claim 1 wherein the bimodal polyethylene composition has a composition distribution breadth index (CDBI₂₅) of greater than 55% by weight.
 9. The process of claim 1 wherein the bimodal polyethylene composition has a composition distribution breadth index (CDBI₅₀) of greater than 65% by weight.
 10. The process of claim 1 wherein the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.5.
 11. The process of claim 1 wherein the bimodal polyethylene composition comprises: from 30 to 60 weight percent of the first ethylene copolymer; and from 70 to 40 weight percent of the second ethylene copolymer.
 12. The process of claim 1 wherein the bimodal polyethylene composition further comprises a nucleating agent or a mixture of nucleating agents.
 13. The process of claim 1 wherein the first and second ethylene copolymers are copolymers of ethylene and 1-octene.
 14. The process of claim 1 wherein the closure is made by continuous compression molding or injection molding.
 15. The process of claim 1 wherein the bimodal polyethylene composition is prepared by contacting ethylene and an alpha-olefin with a polymerization catalyst under solution polymerization conditions in a least two polymerization reactors.
 16. A process to fill a container, the process comprising: adding a hot liquid to the container through a container opening; sealing the container opening with a closure comprising a bimodal polyethylene composition having a density of from 0.949 g/cm³ to 0.960 g/cm³, a molecular weight distribution M_(w)/M_(n), of from 3.0 to 13.0, and a melt index I₂, of from 0.2 to 3.0 g/10 min; and bringing the hot liquid into contact with an interior surface of the closure; wherein the closure has a time exponent, m of 0.105 or less where m is determined using a compressive strain model represented by the equation: ε=A×σ ^(n) ×t ^(m) where ε is the compressive strain; σ is the stress in N/cm², t is the loading time in seconds, A is the model coefficient, n is the deformation stress exponent and m is the time exponent.
 17. The process of claim 16, wherein the bimodal polyethylene composition comprises: (1) 10 to 70 weight percent of a first ethylene copolymer having a melt index I₂, of less than 0.4 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density of from 0.920 to 0.955 g/cm³; and (2) 90 to 30 weight percent of a second ethylene copolymer having a melt index I₂, of from 100 to 20,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.7; and a density higher than the density of the first ethylene copolymer, but less than 0.967 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 0.5. 